Polyethylene compositions and films made therefrom

ABSTRACT

Provided herein are polyethylene compositions with broad orthogonal composition distribution. The polyethylene compositions may comprise at least 65 wt % ethylene-derived units and from 0 to 35 wt % of C 3  to C 12  olefin comonomer-derived units, and furthermore may exhibit a reversed comonomer index (RCI,m) of 100 kg/mol or greater, a Tw 1 -Tw 2  value of from −16 to −38° C., and an Mw 1 /Mw 2  value of at least 0.9, such as 0.9 to 4. Also provided are processes for making the polyethylene compositions, as well as films made from the polyethylene compositions. Such films may feature superior film stiffness for a given polyethylene composition density, and accordingly such films in some embodiments have average MD/TD modulus and density satisfying the following equation: Avg. Modulus≥1.2*(C1*Density−C2), where C1 and C2 are constants, such as C1=2,065,292 and C2=1,872,345.

CROSS-REFERENCE OF RELATED APPLICATIONS

This application claims the benefit of Ser. No. 62/591,557, filed on Nov. 28, 2017, the disclosure of which is incorporated herein by reference in its entirety.

FIELD OF THE INVENTION

The present disclosure relates polyethylene (PE) compositions and films made therefrom.

BACKGROUND OF THE INVENTION

Olefin polymerization catalysts are of great use in industry to produce polyolefin polymers and these polymers have revolutionized virtually every aspect of the modern world. Hence, there is strong interest in finding new catalyst systems to use in polymerization processes that increase the commercial usefulness of the catalyst systems and allow the production of polyolefin polymers having improved properties or a new combination of properties.

In particular, much effort has been placed in understanding how the comonomer is distributed along the polymer carbon chain or simply polymer chain of a polyolefin polymer. For example, the composition distribution of an ethylene alpha-olefin copolymer refers to the distribution of comonomer (short chain branches) among the molecules that comprise the polyethylene polymer. When the amount of short chain branches varies among the polymer carbon chain, the polymer or resin is said to have a Broad Composition Distribution (BCD). When the amount of comonomer per about 1000 carbons is similar among the polyethylene molecules of different polymer chain lengths or molecular weights, the composition distribution is said to be “narrow” or have a Narrow Composition Distribution (NCD).

The composition distribution is known to influence the properties of copolymers, for example, extractables content, environmental stress crack resistance, heat sealing, dart drop impact resistance, and tear resistance or strength. The composition distribution of a polyolefin may be readily measured by methods known in the art, for example, Temperature Raising Elution Fractionation (TREF) or Crystallization Analysis Fractionation (CRYSTAF). See, for example, U.S. Pat. No. 8,378,043, Col. 3 and Col. 4.

Ethylene alpha-olefin copolymers may be produced in a low pressure reactor, utilizing, for example, solution, slurry, and/or gas phase polymerization processes. Polymerization takes place in the presence of activated catalyst systems such as those employing a Ziegler-Natta catalyst, a chromium based catalyst, a vanadium catalyst, a metallocene catalyst, a mixed catalyst (i.e., two or more different catalysts co-supported on the same carrier such as a bimodal catalyst), other advanced catalysts, or combinations thereof. In general, these catalysts when used in a catalyst system all produce a variety of polymer chains in a polyolefin polymer composition that vary in molecular weight and comonomer incorporation. In some cases, this variation becomes a “signature” to the catalyst itself.

For example, it is generally known in the art that a polyolefin's composition distribution is largely dictated by the type of catalyst used. For example, Broad Composition Distribution or BCD refers to polymers in which the length of the molecules would be substantially the same but the amount of the comonomer would vary along the length, for example, for an ethylene-hexene copolymer, hexene distribution varies from low to high while the molecular weight is roughly the same or the Polydispersity Index (PDI) is narrow.

Polymers made with Zeigler Natta catalysts are considered to be “conventional” in which the composition distribution is broad but the high molecular weight fractions are higher density (i.e., less comonomer) than the lower molecular weight fraction (high comonomer).

In contrast, metallocene catalysts typically produce a polyolefin polymer composition with an NCD. A metallocene catalyst is generally a metal complex of a transitional metal, typically, a Group 4 metal, and one or more cyclopentadienyl (Cp) ligands or rings. As stated above, NCD generally refers to the comonomer being evenly distributed or not vary much along the polymer chain. An illustration is provided below. An illustration is provided in FIG. 5 a.

More recently, a third distribution has been described for a polyolefin polymer composition having a Broad Orthogonal Composition Distribution (BOCD) in which the comonomer is incorporated predominantly in the high molecular weight chains. A substituted hafnocene catalyst has been noted to produce this type of distribution. See, for example, U.S. Pat. Nos. 6,242,545, 6,248,845, 6,528,597, 6,936,675, 6,956,088, 7,172,816, 7,179,876, 7,381,783, 8,247,065, 8,378,043, 8,476,392; U.S. Publication No. 2015/0291748; and Ser. No. 62/461,104, filed Feb. 20, 2017, entitled Supported Catalyst Systems and Processes for Use Thereof. An illustration is provided in FIG. 5b . This distribution has been noted for its improved physical properties, for example, ease in fabrication of end-use articles as well as stiffness and toughness in multiple applications such as films that can be measured by dart drop impact resistance and tear resistance or strength.

As taught by U.S. Pat. No. 8,378,043, BOCD refers to incorporating the comonomer predominantly in the high molecular weight chains. The distribution of the short chain branches can be measured, for example, using Temperature Raising Elution Fractionation (TREF) in connection with a Light Scattering (LS) detector to determine the weight average molecular weight of the molecules eluted from the TREF column at a given temperature. The combination of TREF and LS (TREF-LS) yields information about the breadth of the composition distribution and whether the comonomer content increases, decreases, or is uniform across the chains of different molecular weights.

In another patent, U.S. Pat. No. 9,290,593 ('593 patent) teaches that the term “BOCD” is a novel terminology that is currently developed and relates to a polymer structure. The term “BOCD structure” means a structure in which the content of the comonomer such as alpha olefins is mainly high at a high molecular weight main chain, that is, a novel structure in which the content of a short chain branching (SCB) is increased as moving toward the high molecular weight. The '593 patent also teaches a BOCD Index. The BOCD Index may be defined by the following equation: BOCD Index=(Content of SCB at the high molecular weight side−Content of SCB at the low molecular weight side)/(Content of SCB at the low molecular weight side), wherein the “Content of SCB at the high molecular weight side” means the content of the SCB (the number of branches/1000 carbon atoms) included in a polymer chain having a molecular weight of Mw of the polyolefin or more and 1.3×Mw or less, and the “Content of SCB at the low molecular weight side” means the content of the SCB (the number of branches/1000 carbon atoms) included in a polymer chain having a molecular weight of 0.7×Mw of the polyolefin or more and less than Mw. The BOCD Index defined by equation above may be in the range of 1 to 5, preferably 2 to 4, more preferably 2 to 3.5. See, also, FIG. 1 and FIG. 2 of the '593 patent (characterizing BOCD polymer structures using GPC-FTIR data).

BOCD behavior in a polymer composition has been associated with a good balance of mechanical and optical properties and has been an important goal in the development of new polymer products. For example, Linear Low Density Polyethylene (LLDPE) film applications and products strive for a good balance of stiffness, toughness, optical properties (e.g., haze and gloss) and processability. For some LLDPE film applications, sealing performance is also important. Sealing performance is affected mainly by density, it improves as density gets lower, but density has the opposite effect on stiffness. Therefore, to achieve a balanced performance, there is usually a trade-off between stiffness and sealing performance. Thus, to improve sealing performance while maintaining good stiffness remains a challenge. Past efforts have shown that namely molecular weight distribution and comonomer distribution interdependence (MWD×CD) has a strong effect on sealing performance, with narrow CD resin by metallocene catalyst outperforming broad CD resin by conventional catalysts. Other background references include U.S. Publication No. 2009/0156764 and U.S. Pat. Nos. 7,119,153, 7,547,754, 7,572,875, 7,625,982, 8,383,754, 8,691,715, 8,722,567, 8,846,841, 8,940,842, 9,006,367, 9,096,745, 9,115,229, 9,181,369, 9,181,370, 9,217,049, 9,334,350, and 9,447,265.

Thus, there is a need for polyethylene compositions that can exhibit, for example, BOCD behavior to produce films or other useful articles with a good balance of one or more of high stiffness, toughness and sealing performance, as well as good optical properties (e.g., haze and gloss).

SUMMARY OF THE INVENTION

In a class of embodiments, the invention provides for a polyethylene composition comprising at least 65 wt % ethylene derived units and from 0 to 35 wt % of C₃-C₁₂ olefin comonomer derived units, based upon the total weight of the polyethylene composition, wherein the polyethylene composition has:

a) an RCI,m of 100 kg/mol or greater;

b) an internal unsaturation as measured by ¹H NMR less than 0.30 total internal unsaturations per thousand carbon atoms; and

one or both of:

c) a Tw₁-Tw₂ value of from −16 to −38° C.;

d) an Mw₁/Mw₂ value of at least 0.9; and

one or more of the following:

e) a density of from 0.890 g/cm³ to 0.940 g/cm³;

f) a melt index (MI) of from 0.1 g/10 min to 30 g/10 min;

g) a melt index ratio (I₂₁/I₂) of from 10 to 90;

h) an M_(w)/M_(n) of from 2 to 12;

i) an M_(z)/M_(w) of from 2.2 to 5.0;

j) an M_(z)/M_(n) of from 10 to 40; and

k) a g′(vis) of 0.990 or less.

In another class of embodiments, the invention provides for a film made from the polyethylene composition as described above, wherein the film has:

i) a relationship between MD/TD modulus and density that satisfies the following equation: Avg. Modulus≥1.2*(C1*Density−C2); and

ii) a seal initiation temperature at 1 N of ≤98.0° C.

In yet another class of embodiments, the invention provides for a process to make the film as described above.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 is a graph of weight percent as a function of temperature of CFC data, demonstrating the calculation of T_(w1) and T_(w2) for various polymers.

FIG. 2 is a graph of weight average molecular weight as a function of temperature of CFC data, demonstrating the calculation of M_(w1) and M_(w2) for various polymers.

FIG. 3 is a plot of compositional presentation plotting (M_(w1)/M_(w2)) values as a function of (T_(w1)-T_(w2)) values.

FIG. 4 is a plot of average film modulus versus resin density for various inventive and comparative examples.

FIG. 5a is an illustration of a polyolefin with narrow composition distribution (NCD).

FIG. 5b is an illustration of a polyolefin with narrow composition distribution (NCD).

DETAILED DESCRIPTION

Before the present compounds, components, compositions, and/or methods are disclosed and described, it is to be understood that unless otherwise indicated this invention is not limited to specific compounds, components, compositions, reactants, reaction conditions, ligands, metallocene structures, catalyst structures, or the like, as such may vary, unless otherwise specified. It is also to be understood that the terminology used herein is for the purpose of describing particular embodiments only and is not intended to be limiting.

In several classes of embodiments of the invention, the present disclosure is directed to catalyst systems and their use in polymerization processes to produce polyolefin polymers such as polyethylene polymers and polypropylene polymers. In another class of embodiments, the present disclosure is directed to polymerization processes to produce polyolefin polymers from catalyst systems comprising the product of the combination of one or more olefin polymerization catalysts, at least one activator, and at least one support.

In particular, the present disclosure is directed to a polymerization process to produce a polyethylene polymer, the process comprising contacting a catalyst system comprising the product of the combination of one or more metallocene catalysts, at least one activator, and at least one support, with ethylene and one or more C₃-C₁₀ alpha-olefin comonomers under polymerizable conditions.

Definitions

For purposes of this invention and the claims hereto, the numbering scheme for the Periodic Table Groups is according to the new notation of the IUPAC Periodic Table of Elements.

As used herein, “olefin polymerization catalyst(s) refers to any catalyst, typically an organometallic complex or compound that is capable of coordination polymerization addition where successive monomers are added in a monomer chain at the organometallic active center.

The terms “substituent,” “radical,” “group,” and “moiety” may be used interchangeably.

As used herein, and unless otherwise specified, the term “C_(n)” means hydrocarbon(s) having n carbon atom(s) per molecule, wherein n is a positive integer.

As used herein, and unless otherwise specified, the term “hydrocarbon” means a class of compounds containing hydrogen bound to carbon, and encompasses (i) saturated hydrocarbon compounds, (ii) unsaturated hydrocarbon compounds, and (iii) mixtures of hydrocarbon compounds (saturated and/or unsaturated), including mixtures of hydrocarbon compounds having different values of n.

The terms “hydrocarbyl radical,” “hydrocarbyl,” “hydrocarbyl group,” “alkyl radical,” and “alkyl” are used interchangeably throughout this document. Likewise, the terms “group,” “radical,” and “substituent,” are also used interchangeably in this document. For purposes of this disclosure, “hydrocarbyl radical” is defined to be C₁-C₁₀₀ radicals, that may be linear, branched, or cyclic, and when cyclic, aromatic or non-aromatic. Examples of such radicals include, but are not limited to, methyl, ethyl, n-propyl, isopropyl, n-butyl, isobutyl, sec-butyl, tert-butyl, pentyl, iso-amyl, hexyl, octyl cyclopropyl, cyclobutyl, cyclopentyl, cyclohexyl, cyclooctyl, and the like including their substituted analogues. Substituted hydrocarbyl radicals are radicals in which at least one hydrogen atom of the hydrocarbyl radical has been substituted with at least one heteroatom or heteroatom containing group, such as halogen (such as Br, Cl, F or I) or at least one functional group such as NR*₂, OR*, SeR*, TeR*, PR*₂, AsR*₂, SbR*₂, SR*, BR*₂, SiR*₃, GeR*₃, SnR*₃, PbR*₃, and the like, or where at least one heteroatom has been inserted within a hydrocarbyl ring.

As used herein, and unless otherwise specified, the term “alkyl” refers to a saturated hydrocarbon radical having from 1 to 12 carbon atoms (i.e., C₁-C₁₂ alkyl), particularly from 1 to 8 carbon atoms (i.e., C₁-C₈ alkyl), particularly from 1 to 6 carbon atoms (i.e., C₁-C₆ alkyl), and particularly from 1 to 4 carbon atoms (i.e., C₁-C₄ alkyl). Examples of alkyl groups include, but are not limited to, methyl, ethyl, propyl, butyl, pentyl, hexyl, heptyl, octyl, decyl, and so forth. The alkyl group may be linear, branched or cyclic. “Alkyl” is intended to embrace all structural isomeric forms of an alkyl group. For example, as used herein, propyl encompasses both n-propyl and isopropyl; butyl encompasses n-butyl, sec-butyl, isobutyl and tert-butyl and so forth. As used herein, “C₁ alkyl” refers to methyl (—CH₃), “C₂ alkyl” refers to ethyl (—CH₂CH₃), “C₃ alkyl” refers to propyl (—CH₂CH₂CH₃) and “C₄ alkyl” refers to butyl (e.g., —CH₂CH₂CH₂CH₃, —(CH₃)CHCH₂CH₃, —CH₂CH(CH₃)₂, etc.). Further, as used herein, “Me” refers to methyl, and “Et” refers to ethyl, “i-Pr” refers to isopropyl, “t-Bu” refers to tert-butyl, and “Np” refers to neopentyl.

As used herein, and unless otherwise specified, the term “alkylene” refers to a divalent alkyl moiety containing 1 to 12 carbon atoms (i.e., C₁-C₁₂ alkylene) in length and meaning the alkylene moiety is attached to the rest of the molecule at both ends of the alkyl unit. For example, alkylenes include, but are not limited to, —CH₂—, —CH₂CH₂—, —CH(CH₃)CH₂—, —CH₂CH₂CH₂—, etc. The alkylene group may be linear or branched.

As used herein, and unless otherwise specified, the term “alkenyl” refers to an unsaturated hydrocarbon radical having from 2 to 12 carbon atoms (i.e., C₂-C₁₂ alkenyl), particularly from 2 to 8 carbon atoms (i.e., C₂-C₈ alkenyl), particularly from 2 to 6 carbon atoms (i.e., C₂-C₆ alkenyl), and having one or more (e.g., 2, 3, etc.,) carbon-carbon double bonds. The alkenyl group may be linear, branched or cyclic. Examples of alkenyls include, but are not limited to ethenyl (vinyl), 2-propenyl, 3-propenyl, 1,4-pentadienyl, 1,4-butadienyl, 1-butenyl, 2-butenyl and 3-butenyl. “Alkenyl” is intended to embrace all structural isomeric forms of an alkenyl. For example, butenyl encompasses 1,4-butadienyl, 1-butenyl, 2-butenyl and 3-butenyl, etc.

As used herein, and unless otherwise specified, the term “alkenylene” refers to a divalent alkenyl moiety containing 2 to about 12 carbon atoms (i.e., C₂-C₁₂ alkenylene) in length and meaning that the alkylene moiety is attached to the rest of the molecule at both ends of the alkyl unit. For example, alkenylenes include, but are not limited to, —CH═CH—, —CH═CHCH₂—, —CH═CH═CH—, —CH₂CH₂CH═CHCH₂—, etc. The alkenylene group may be linear or branched.

As used herein, and unless otherwise specified, the term “alkynyl” refers to an unsaturated hydrocarbon radical having from 2 to 12 carbon atoms (i.e., C₂-C₁₂ alkynyl), particularly from 2 to 8 carbon atoms (i.e., C₂-C₈ alkynyl), particularly from 2 to 6 carbon atoms (i.e., C₂-C₆ alkynyl), and having one or more (e.g., 2, 3, etc.) carbon-carbon triple bonds. The alkynyl group may be linear, branched or cyclic. Examples of alkynyls include, but are not limited to ethynyl, 1-propynyl, 2-butynyl, and 1,3-butadiynyl. “Alkynyl” is intended to embrace all structural isomeric forms of an alkynyl. For example, butynyl encompasses 2-butynyl, and 1,3-butadiynyl and propynyl encompasses 1-propynyl and 2-propynyl (propargyl).

As used herein, and unless otherwise specified, the term “alkynylene” refers to a divalent alkynyl moiety containing 2 to about 12 carbon atoms (i.e., C₂-C₁₂ alkenylene) in length and meaning that the alkylene moiety is attached to the rest of the molecule at both ends of the alkyl unit. For example, alkenylenes include, but are not limited to, —C≡C—, —C≡CCH₂—, —C≡CCH₂C≡C—, —CH₂CH₂C≡CCH₂—. The alkynylene group may be linear or branched.

As used herein, and unless otherwise specified, the term “alkoxy” refers to —O— alkyl containing from 1 to about 10 carbon atoms. The alkoxy may be straight-chain or branched-chain. Non-limiting examples include methoxy, ethoxy, propoxy, butoxy, isobutoxy, tert-butoxy, pentoxy, and hexoxy. “C₁ alkoxy” refers to methoxy, “C₂ alkoxy” refers to ethoxy, “C₃ alkoxy” refers to propoxy and “C₄ alkoxy” refers to butoxy. Further, as used herein, “OMe” refers to methoxy and “OEt” refers to ethoxy.

As used herein, and unless otherwise specified, the term “aromatic” refers to unsaturated cyclic hydrocarbons having a delocalized conjugated it system and having from 5 to 20 carbon atoms (aromatic C₅-C₂₀ hydrocarbon), particularly from 5 to 12 carbon atoms (aromatic C₅-C₁₂ hydrocarbon), and particularly from 5 to 10 carbon atoms (aromatic C₅-C₁₂ hydrocarbon). Exemplary aromatics include, but are not limited to benzene, toluene, xylenes, mesitylene, ethylbenzenes, cumene, naphthalene, methylnaphthalene, dimethylnaphthalenes, ethylnaphthalenes, acenaphthalene, anthracene, phenanthrene, tetraphene, naphthacene, benzanthracenes, fluoranthrene, pyrene, chrysene, triphenylene, and the like, and combinations thereof.

Unless otherwise indicated, where isomers of a named alkyl, alkenyl, alkoxy, or aryl group exist (e.g., n-butyl, iso-butyl, sec-butyl, and tert-butyl) reference to one member of the group (e.g., n-butyl) shall expressly disclose the remaining isomers (e.g., iso-butyl, sec-butyl, and tert-butyl) in the family. Likewise, reference to an alkyl, alkenyl, alkoxide, or aryl group without specifying a particular isomer (e.g., butyl) expressly discloses all isomers (e.g., n-butyl, iso-butyl, sec-butyl, and tert-butyl).

As used herein, the term “hydroxyl” refers to an —OH group.

As used herein, “oxygenate” refers to a saturated, unsaturated, or polycyclic cyclized hydrocarbon radical containing from 1 to 40 carbon atoms and further containing one or more oxygen heteroatoms.

As used herein, “aluminum alkyl adducts” refers to the reaction product of aluminum alkyls and/or alumoxanes with quenching agents, such as water and/or methanol.

An “olefin,” alternatively referred to as “alkene,” is a linear, branched, or cyclic compound of carbon and hydrogen having at least one double bond. For purposes of this specification and the claims appended thereto, when a polymer or copolymer is referred to as comprising an olefin, the olefin present in such polymer or copolymer is the polymerized form of the olefin. For example, when a copolymer is said to have an “ethylene” content of 35 wt % to 55 wt %, it is understood that the mer unit in the copolymer is derived from ethylene in the polymerization reaction and said derived units are present at 35 wt % to 55 wt %, based upon the weight of the copolymer.

A “polymer” has two or more of the same or different mer units. A “homopolymer” is a polymer having mer units that are the same. A “copolymer” is a polymer having two or more mer units that are distinct or different from each other. A “terpolymer” is a polymer having three mer units that are distinct or different from each other. “Distinct” or “different” as used to refer to mer units indicates that the mer units differ from each other by at least one atom or are different isomerically. Accordingly, the definition of copolymer, as used herein, includes terpolymers and the like. An “ethylene polymer” or “ethylene copolymer” is a polymer or copolymer comprising at least 50 mol % ethylene derived units, a “propylene polymer” or “propylene copolymer” is a polymer or copolymer comprising at least 50 mol % propylene derived units, and so on.

“Polymerizable conditions” refer those conditions including a skilled artisan's selection of temperature, pressure, reactant concentrations, optional solvent/diluents, reactant mixing/addition parameters, and other conditions within at least one polymerization reactor that are conducive to the reaction of one or more olefin monomers when contacted with an activated olefin polymerization catalyst to produce the desired polyolefin polymer through typically coordination polymerization.

The term “continuous” means a system that operates without interruption or cessation. For example a continuous process to produce a polymer would be one where the reactants are continually introduced into one or more reactors and polymer product is continually withdrawn.

A “catalyst composition” or “catalyst system” is the combination of at least one catalyst compound, a support material, an optional activator, and an optional co-activator. For the purposes of this invention and the claims thereto, when catalyst systems or compositions are described as comprising neutral stable forms of the components, it is well understood by one of ordinary skill in the art, that the ionic form of the component is the form that reacts with the monomers to produce polymers. When it is used to describe such after activation, it means the support, the activated complex, and the activator or other charge-balancing moiety. The transition metal compound may be neutral as in a precatalyst, or a charged species with a counter ion as in an activated catalyst system.

Coordination polymerization is an addition polymerization in which successive monomers are added to or at an organometallic active center to create and/or grow a polymer chain.

The terms “cocatalyst” and “activator” are used herein interchangeably and are defined to be any compound which can activate any one of the catalyst compounds herein by converting the neutral catalyst compound to a catalytically active catalyst compound cation.

The term “contact product” or “the product of the combination of” is used herein to describe compositions wherein the components are contacted together in any order, in any manner, and for any length of time. For example, the components can be contacted by blending or mixing. Further, contacting of any component can occur in the presence or absence of any other component of the compositions described herein. Combining additional materials or components can be done by any suitable method. Further, the term “contact product” includes mixtures, blends, solutions, slurries, reaction products, and the like, or combinations thereof. Although “contact product” can include reaction products, it is not required for the respective components to react with one another or react in the manner as theorized. Similarly, the term “contacting” is used herein to refer to materials which may be blended, mixed, slurried, dissolved, reacted, treated, or otherwise contacted in some other manner.

Certain abbreviations may be used to for the sake of brevity and include but are not limited to Me=methyl, Et=ethyl, Pr=propyl, Bu=butyl, Ph=phenyl, Cp=cyclopentadienyl, Cp*=pentamethyl cydopentadienyl, Ind=indenyl, etc.

“BOCD” refers to a Broad Orthogonal Composition Distribution in which the comonomer of a copolymer is incorporated predominantly in the high molecular weight chains or species of a polyolefin polymer or composition. The distribution of the short chain branches can be measured, for example, using Temperature Raising Elution Fractionation (TREF) in connection with a Light Scattering (LS) detector to determine the weight average molecular weight of the molecules eluted from the TREF column at a given temperature. The combination of TREF and LS (TREF-LS) yields information about the breadth of the composition distribution and whether the comonomer content increases, decreases, or is uniform across the chains of different molecular weights of polymer chains. BOCD has been described, for example, in U.S. Pat. No. 8,378,043, Col. 3, line 34, bridging Col. 4, line 19, and U.S. Pat. No. 8,476,392, line 43, bridging Col. 16, line 54.

The breadth of the composition distribution is characterized by the T₇₅−T₂₅ value, wherein T₂₅ is the temperature at which 25% of the eluted polymer is obtained and T₇₅ is the temperature at which 75% of the eluted polymer is obtained in a TREF experiment as described herein. The composition distribution is further characterized by the F₈₀ value, which is the fraction of polymer that elutes below 80° C. in a TREF-LS experiment as described herein. A higher F₈₀ value indicates a higher fraction of comonomer in the polymer molecule. An orthogonal composition distribution is defined by a M₆₀/M₉₀ value that is greater than 1, wherein M₆₀ is the molecular weight of the polymer fraction that elutes at 60° C. in a TREF-LS experiment and M₉₀ is the molecular weight of the polymer fraction that elutes at 90° C. in a TREF-LS experiment as described herein.

In a class of embodiments, the polymers as described herein may have a BOCD characterized in that the T₇₅−T₂₅ value is 1 or greater, 2.0 or greater, 2.5 or greater, 4.0 or greater, 5.0 or greater, 7.0 or greater, 10.0 or greater, 11.5 or greater, 15.0 or greater, 17.5 or greater, 20.0 or greater, 25.0 or greater, 30.0 or greater, 35.0 or greater, 40.0 or greater, or 45.0 or greater, wherein T₂₅ is the temperature at which 25% of the eluted polymer is obtained and T₇₅ is the temperature at which 75% of the eluted polymer is obtained in a TREF experiment as described herein.

The polymers as described herein may further have a BOCD characterized in that M₆₀/M₉₀ value is 1.5 or greater, 2.0 or greater, 2.25 or greater, 2.50 or greater, 3.0 or greater, 3.5 or greater, 4.0 or greater, 4.5 or greater, or 5.0 or greater, wherein M₆₀ is the molecular weight of the polymer fraction that elutes at 60° C. in a TREF-LS experiment and M₉₀ is the molecular weight of the polymer fraction that elutes at 90° C. in a TREF-LS experiment as described herein.

Additionally, the polymers as described herein may further have a BOCD characterized in that F₈₀ value is 1% or greater, 2% or greater, 3% or greater, 4% or greater, 5% or greater, 6% or greater, 7% or greater, 10% or greater, 11% or greater, 12% or greater, or 15% or greater, wherein F₈₀ is the fraction of polymer that elutes below 80° C.

Olefin Polymerization Catalysts

Metallocene Catalysts

In a class of embodiments, the catalyst system may be a mixed metallocene catalyst system (i.e., comprising more than one catalyst) and comprise two or more catalysts described below. In particular, the catalyst system may comprise the product of the combination of: a) a first metallocene catalyst and a second metallocene catalyst independently selected and represented by the formula

wherein: M is a Group 4-6 metal; each X¹ and X² is, independently, a hydrocarbyl radical having from 1 to 20 carbon atoms, hydride, amide, alkoxide, sulfide, phosphide, halide, diene, amine, phosphine, ether, or X¹ and X² is part of a fused ring structure; each of R¹, R², R³, R⁴, R⁶, R⁷, R⁸, and R⁹ is, independently, a hydrogen, halide, alkoxide or a C₁ to C₄₀ substituted or unsubstituted hydrocarbyl group, or a pair of R¹, R², R³, R⁴, R⁶, R⁷, R⁸, and R⁹ form a substituted or unsubstituted fused ring structure; T is a bridging group comprising, independently, one or more Group 14-16 atoms; and each R^(a) and R^(b) is optional and independently, a hydrocarbyl or a substituted hydrocarbyl; wherein the bridging group T of the second metallocene catalyst comprises at least two Group 14-16 atoms and at least one more Group 14-16 atom than the bridging group T of the first metallocene catalyst.

In any of the embodiments described herein, the bridging group T of the first metallocene catalyst is selected from Group 14 atoms, for example, a silicon or a germanium atom. Each R^(a) and R^(b) of the first metallocene catalyst may be a substituted or unsubstituted C₁ to C₂₀ alkyl, a C₆ to C₂₀ substituted or unsubstituted aryl, for example, each R^(a) and R^(b) of the first metallocene catalyst may be selected from the group consisting of substituted or unsubstituted C₁ to C₁₂ alkyl groups, phenyl groups, and substituted phenyl groups. In an embodiment, each R^(a) and R^(b) of the first metallocene catalyst are phenyl groups.

In any of the embodiments described herein, the bridging group T of the second metallocene catalyst may comprise at least two more Group 14-16 atoms than the bridging group T of the first metallocene catalyst, for example, the bridging group T of the second metallocene catalyst may comprise a Si—O—Si or a Si—N—Si group. In an embodiment, the bridging group T of the second metallocene catalyst may comprise at least one oxygen atom and at least two silicon atoms. Each R^(a) and R^(b) of the second metallocene catalyst may be a substituted or unsubstituted C₁ to C₂₀ alkyl, a C₆ to C₂₀ substituted or unsubstituted aryl, for example, each R^(a) and R^(b) of the second metallocene catalyst may be selected from the group consisting of substituted or unsubstituted C₁ to C₁₂ alkyl groups, phenyl groups, and substituted phenyl groups. In an embodiment, each R^(a) and R^(b) of the second metallocene catalyst are methyl groups. The bridging group T of the second metallocene catalyst may comprise at least one unsubstituted Group 14-16 atom.

In any of the embodiments described herein, each of R¹, R², R³, R⁴, R⁶, R⁷, R⁸, and R⁹ of either the first metallocene catalyst and/or the second metallocene catalyst is, independently, a C₁ to C₂₀ substituted or unsubstituted hydrocarbyl group. At least two of R¹, R², R³, R⁴, R⁶, R⁷, R⁸, and R⁹ of either the first metallocene catalyst and/or the second metallocene catalyst may be a linear C₃ to C₂₀ substituted or unsubstituted hydrocarbyl group, for example, at least one of R² and R³ and at least one of R⁷ and R⁸ of either the first metallocene catalyst and/or the second metallocene catalyst may be a C₃ to C₁₀ linear alkyl group. C₃ to C₁₀ linear alkyl group include n-propyl, n-butyl, n-pentyl, n-hexyl, n-heptyl, n-octyl, n-nonyl, n-decyl group, or a combination thereof.

In any of the embodiments described herein, M is a Group 4 metal, such as hafnium or zirconium. In a class of embodiments, the metal of the first metallocene catalyst is hafnium and the metal of the second metallocene is zirconium. In the same or another class of embodiments, the first metallocene catalyst may be a rac, meso-metallocene catalyst or catalyst mixture and the second metallocene may be a meso-metallocene catalyst.

One or more of the metallocene catalyst as described above or below may be used in a mixed catalyst system also known as a dual catalyst system comprising, for example, two or three metallocene catalysts or any of the catalysts described herein or known in the art to be useful for olefin polymerization. They may co-supported, that is disposed on the same or different support material, optionally and in addition to, injected into the reactor(s) separately (with or without a support) or in different combinations and proportions together to “trim” or adjust the polymer product properties according to its target specification. This approach is very useful in controlling polymer product properties and insuring uniformity in high volume production of polyolefin polymers.

Activators

The catalyst compositions may be combined with activators in any manner in the art including by supporting them for use in slurry or gas phase polymerization. Activators are generally compounds that can activate any one of the catalyst compounds described above by converting the neutral metal compound to a catalytically active metal compound cation. Non-limiting activators, for example, include alumoxanes, aluminum alkyls, ionizing activators, which may be neutral or ionic, and conventional-type cocatalysts. Preferred activators typically include alumoxane compounds, modified alumoxane compounds, and ionizing anion precursor compounds that abstract a reactive, σ-bound, metal ligand making the metal compound cationic and providing a charge-balancing non-coordinating or weakly coordinating anion.

Alumoxane Activators

Alumoxane activators are utilized as activators in the catalyst compositions described herein. Alumoxanes are generally oligomeric compounds containing —Al(R¹)—O-sub-units, where R¹ is an alkyl group. Examples of alumoxanes include methylalumoxane (MAO), modified methylalumoxane (MMAO), ethylalumoxane and isobutylalumoxane. Alkylalumoxanes and modified alkylalumoxanes are suitable as catalyst activators, particularly when the abstractable ligand is an alkyl, halide, alkoxide or amide. Mixtures of different alumoxanes and modified alumoxanes may also be used. It may be preferable to use a visually clear methylalumoxane. A cloudy or gelled alumoxane can be filtered to produce a clear solution or clear alumoxane can be decanted from the cloudy solution. A useful alumoxane is a modified methyl alumoxane (MMAO) cocatalyst type 3A (commercially available from Akzo Chemicals, Inc. under the trade name Modified Methylalumoxane type 3A, covered under U.S. Pat. No. 5,041,584).

When the activator is an alumoxane (modified or unmodified), some embodiments select the maximum amount of activator typically at up to a 5000-fold molar excess Al/M over the catalyst compound (per metal catalytic site). The minimum activator-to-catalyst-compound is a 1:1 molar ratio. Alternate preferred ranges include from 1:1 to 500:1, alternately from 1:1 to 200:1, alternately from 1:1 to 100:1, or alternately from 1:1 to 50:1.

In class of embodiments, little or no alumoxane is used in the polymerization processes described herein. Preferably, alumoxane is present at zero mol %, alternatively, the alumoxane is present at a molar ratio of aluminum to catalyst compound transition metal less than 500:1, preferably less than 300:1, preferably less than 100:1, and preferably less than 1:1.

In another class of embodiments, the at least one activator comprises aluminum and the aluminum to transition metal, for example, hafnium or zirconium, ratio is at least 150 to 1; the at least one activator comprises aluminum and the aluminum to transition metal, for example, hafnium or zirconium, ratio is at least 250 to 1; or the at least one activator comprises aluminum and the aluminum to transition metal, for example, hafnium or zirconium, ratio is at least 1,000 to 1.

Ionizing/Non Coordinating Anion Activators

The term “non-coordinating anion” (NCA) means an anion which either does not coordinate to a cation or which is only weakly coordinated to a cation thereby remaining sufficiently labile to be displaced by a neutral Lewis base. “Compatible” non-coordinating anions are those which are not degraded to neutrality when the initially formed complex decomposes. Further, the anion will not transfer an anionic substituent or fragment to the cation so as to cause it to form a neutral transition metal compound and a neutral by-product from the anion. Non-coordinating anions useful in accordance with this invention are those that are compatible, stabilize the transition metal cation in the sense of balancing its ionic charge at +1, and yet retain sufficient lability to permit displacement during polymerization. Ionizing activators useful herein typically comprise an NCA, particularly a compatible NCA.

It is within the scope of this invention to use an ionizing activator, neutral or ionic, such as tri (n-butyl) ammonium tetrakis (pentafluorophenyl) borate, a tris perfluorophenyl boron metalloid precursor or a tris perfluoronaphthyl boron metalloid precursor, polyhalogenated heteroborane anions (WO 98/43983), boric acid (U.S. Pat. No. 5,942,459), or combination thereof. It is also within the scope of this invention to use neutral or ionic activators alone or in combination with alumoxane or modified alumoxane activators.

For descriptions of useful activators please see U.S. Pat. Nos. 8,658,556 and 6,211,105.

Preferred activators include N,N-dimethylanilinium tetrakis(perfluoronaphthyl)borate, N,N-dimethylanilinium tetrakis(perfluorobiphenyl)borate, N,N-dimethylanilinium tetrakis(perfluorophenyl)borate, N,N-dimethylanilinium tetrakis(3,5-bis(trifluoromethyl)phenyl)borate, triphenylcarbenium tetrakis(perfluoronaphthyl)borate, triphenylcarbenium tetrakis(perfluorobiphenyl)borate, triphenylcarbenium tetrakis(3,5-bis(trifluoromethyl)phenyl)borate, triphenylcarbenium tetrakis(perfluorophenyl)borate, [Me₃NH⁺][B(C₆F₅)₄ ⁻]; 1-(4-(tris(pentafluorophenyl)borate)-2,3,5,6-tetrafluorophenyl)pyrrolidinium; and tetrakis(pentafluorophenyl)borate, 4-(tris(pentafluorophenyl)borate)-2,3,5,6-tetrafluoropyridine.

In a preferred embodiment, the activator comprises a triaryl carbonium (such as triphenylcarbenium tetraphenylborate, triphenylcarbenium tetrakis(pentafluorophenyl)borate, triphenylcarbenium tetrakis-(2,3,4,6-tetrafluorophenyl)borate, triphenylcarbenium tetrakis(perfluoronaphthyl)borate, triphenylcarbenium tetrakis(perfluorobiphenyl)borate, triphenylcarbenium tetrakis(3,5-bis(trifluoromethyl)phenyl)borate).

In another embodiment, the activator comprises one or more of trialkylammonium tetrakis(pentafluorophenyl)borate, N,N-dialkylanilinium tetrakis(pentafluorophenyl)borate, N,N-dimethyl-(2,4,6-trimethylanilinium) tetrakis(pentafluorophenyl)borate, trialkylammonium tetrakis-(2,3,4,6-tetrafluorophenyl) borate, N,N-dialkylanilinium tetrakis-(2,3,4,6-tetrafluorophenyl)borate, trialkylammonium tetrakis(perfluoronaphthyl)borate, N,N-dialkylanilinium tetrakis(perfluoronaphthyl)borate, trialkylammonium tetrakis(perfluorobiphenyl)borate, N,N-dialkylanilinium tetrakis(perfluorobiphenyl)borate, trialkylammonium tetrakis(3,5-bis(trifluoromethyl)phenyl)borate, N,N-dialkylanilinium tetrakis(3,5-bis(trifluoromethyl)phenyl)borate, N,N-dialkyl-(2,4,6-trimethylanilinium) tetrakis(3,5-bis(trifluoromethyl)phenyl)borate, di-(i-propyl)ammonium tetrakis(pentafluorophenyl)borate, (where alkyl is methyl, ethyl, propyl, n-butyl, sec-butyl, or t-butyl).

The typical activator-to-catalyst ratio, e.g., all NCA activators-to-catalyst ratio is about a 1:1 molar ratio. Alternate preferred ranges include from 0.1:1 to 100:1, alternately from 0.5:1 to 200:1, alternately from 1:1 to 500:1 alternately from 1:1 to 1000:1. A particularly useful range is from 0.5:1 to 10:1, preferably 1:1 to 5:1.

Support Materials

The catalyst composition may optionally comprise at least one “support” or sometimes also referred to as a “carrier”. The terms may be interchangeable unless otherwise distinguished. Suitable supports, include but are not limited to silica, alumina, silica-alumina, zirconia, titania, silica-alumina, cerium oxide, magnesium oxide, or combinations thereof. The catalyst may optionally comprise a support or be disposed on at least one support. Suitable supports, include but are not limited to, active and inactive materials, synthetic or naturally occurring zeolites, as well as inorganic materials such as clays and/or oxides such as silica, alumina, zirconia, titania, silica-alumina, cerium oxide, magnesium oxide, or combinations thereof. In particular, the support may be silica-alumina, alumina and/or a zeolite, particularly alumina. Silica-alumina may be either naturally occurring or in the form of gelatinous precipitates or gels including mixtures of silica and metal oxides.

In class of embodiments, the at least one support may comprise an organosilica material. The organosilica material supports may be a polymer formed of at least one monomer. In certain embodiments, the organosilica material may be a polymer formed of multiple distinct monomers. Methods and materials for producing the organosilica materials as well as a characterization description may be found in, for example, WO 2016/094770 and WO 2016 094774.

Scavengers, Chain Transfer Agents and/or Co-Activators

Scavengers, chain transfer agents, or co-activators may also be used. Aluminum alkyl compounds which may be utilized as scavengers or co-activators include, for example, one or more of those represented by the formula AlR₃, where each R is, independently, a C₁-C₈ aliphatic radical, preferably methyl, ethyl, propyl, butyl, pentyl, hexyl octyl or an isomer thereof), especially trimethylaluminum, triethylaluminum, triisobutylaluminum, tri-n-hexylaluminum, tri-n-octylaluminum or mixtures thereof.

Useful chain transfer agents that may also be used herein are typically a compound represented by the formula AlR²⁰ ₃, ZnR²⁰ ₂ (where each R²⁰ is, independently, a C₁-C₈ aliphatic radical, preferably methyl, ethyl, propyl, butyl, pentyl, hexyl octyl or an isomer thereof) or a combination thereof, such as diethyl zinc, trimethylaluminum, triisobutylaluminum, trioctylaluminum, or a combination thereof.

Polymerization Processes

In embodiments herein, the invention relates to polymerization processes where monomer (such as propylene and or ethylene), and optionally comonomer, are contacted with a catalyst system comprising at least one activator, at least one support and at least one catalyst, such as a metallocene compound, as described above. The support, catalyst compound, and activator may be combined in any order, and are combined typically prior to contacting with the monomers.

Monomers useful herein include substituted or unsubstituted C₂ to C₄₀ alpha olefins, preferably C₂ to C₂₀ alpha olefins, preferably C₂ to C₁₂ alpha olefins, preferably ethylene, propylene, butene, pentene, hexene, heptene, octene, nonene, decene, undecene, dodecene and isomers thereof.

In an embodiment of the invention, the monomer comprises propylene and an optional comonomers comprising one or more ethylene or C₄ to C₄₀ olefins, preferably C₄ to C₂₀ olefins, or preferably C₆ to C₁₂ olefins. The C₄ to C₄₀ olefin monomers may be linear, branched, or cyclic. The C₄ to C₄₀ cyclic olefins may be strained or unstrained, monocyclic or polycyclic, and may optionally include heteroatoms and/or one or more functional groups.

In another embodiment of the invention, the monomer comprises ethylene and optional comonomers comprising one or more C₃ to C₄₀ olefins, preferably C₄ to C₂₀ olefins, or preferably C₆ to C₁₂ olefins. The C₃ to C₄₀ olefin monomers may be linear, branched, or cyclic. The C₃ to C₄₀ cyclic olefins may be strained or unstrained, monocyclic or polycyclic, and may optionally include heteroatoms and/or one or more functional groups.

Exemplary C₂ to C₄₀ olefin monomers and optional comonomers include ethylene, propylene, butene, pentene, hexene, heptene, octene, nonene, decene, undecene, dodecene, norbomene, norbomadiene, dicyclopentadiene, cyclopentene, cycloheptene, cyclooctene, cyclooctadiene, cyclododecene, 7-oxanorbomene, 7-oxanorbomadiene, substituted derivatives thereof, and isomers thereof, preferably hexene, heptene, octene, nonene, decene, dodecene, cyclooctene, 1,5-cyclooctadiene, 1-hydroxy-4-cyclooctene, 1-acetoxy-4-cyclooctene, 5-methylcyclopentene, cyclopentene, dicyclopentadiene, norbomene, norbomadiene, and their respective homologs and derivatives, preferably norbomene, norbomadiene, and dicyclopentadiene.

In a preferred embodiment one or more dienes are present in the polymer produced herein at up to 10 wt %, preferably at 0.00001 to 1.0 wt %, preferably 0.002 to 0.5 wt %, even more preferably 0.003 to 0.2 wt %, based upon the total weight of the composition. In some embodiments 500 ppm or less of diene is added to the polymerization, preferably 400 ppm or less, preferably or 300 ppm or less. In other embodiments at least 50 ppm of diene is added to the polymerization, or 100 ppm or more, or 150 ppm or more.

Diolefin monomers useful in this invention include any hydrocarbon structure, preferably C₄ to C₃₀, having at least two unsaturated bonds, wherein at least two of the unsaturated bonds are readily incorporated into a polymer by either a stereospecific or a non-stereospecific catalyst(s). It is further preferred that the diolefin monomers be selected from alpha, omega-diene monomers (i.e., di-vinyl monomers). More preferably, the diolefin monomers are linear di-vinyl monomers, most preferably those containing from 4 to 30 carbon atoms. Examples of preferred dienes include butadiene, pentadiene, hexadiene, heptadiene, octadiene, nonadiene, decadiene, undecadiene, dodecadiene, tridecadiene, tetradecadiene, pentadecadiene, hexadecadiene, heptadecadiene, octadecadiene, nonadecadiene, icosadiene, heneicosadiene, docosadiene, tricosadiene, tetracosadiene, pentacosadiene, hexacosadiene, heptacosadiene, octacosadiene, nonacosadiene, triacontadiene, particularly preferred dienes include 1,6-heptadiene, 1,7-octadiene, 1,8-nonadiene, 1,9-decadiene, 1,10-undecadiene, 1,11-dodecadiene, 1,12-tridecadiene, 1,13-tetradecadiene, and low molecular weight polybutadienes (M_(w) less than 1000 g/mol). Preferred cyclic dienes include cyclopentadiene, vinylnorbomene, norbomadiene, ethylidene norbornene, divinylbenzene, dicyclopentadiene or higher ring containing diolefins with or without substituents at various ring positions.

Polymerization processes according to the present disclosure can be carried out in any manner known in the art. Any suspension, slurry, high pressure tubular or autoclave process, or gas phase polymerization process known in the art can be used under polymerizable conditions. Such processes can be run in a batch, semi-batch, or continuous mode. Heterogeneous polymerization processes (such as gas phase and slurry phase processes) are useful. A heterogeneous process is defined to be a process where the catalyst system is not soluble in the reaction media. Alternatively, in other embodiments, the polymerization process is not homogeneous.

A homogeneous polymerization process is defined to be a process where preferably at least 90 wt % of the product is soluble in the reaction media. Alternatively, the polymerization process is not a bulk process is particularly preferred. In a class of embodiments, a bulk process is defined to be a process where monomer concentration in all feeds to the reactor is preferably 70 vol % or more. Alternatively, no solvent or diluent is present or added in the reaction medium, (except for the small amounts used as the carrier for the catalyst system or other additives, or amounts typically found with the monomer; e.g., propane in propylene). In another embodiment, the process is a slurry process. As used herein the term “slurry polymerization process” means a polymerization process where a supported catalyst is employed and monomers are polymerized on the supported catalyst particles. At least 95 wt % of polymer products derived from the supported catalyst are in granular form as solid particles (not dissolved in the diluent).

Suitable diluents/solvents for polymerization include non-coordinating, inert liquids. Examples include straight and branched-chain hydrocarbons, such as isobutane, butane, pentane, isopentane, hexanes, isohexane, heptane, octane, dodecane, and mixtures thereof; cyclic and alicyclic hydrocarbons, such as cyclohexane, cycloheptane, methylcyclohexane, methylcycloheptane, and mixtures thereof, such as can be found commercially (Isopar™); perhalogenated hydrocarbons, such as perfluorinated C₄₋₁₀ alkanes, chlorobenzene, and aromatic and alkylsubstituted aromatic compounds, such as benzene, toluene, mesitylene, and xylene. Suitable solvents also include liquid olefins which may act as monomers or comonomers including ethylene, propylene, 1-butene, 1-hexene, 1-pentene, 3-methyl-1-pentene, 4-methyl-1-pentene, 1-octene, 1-decene, and mixtures thereof. In a preferred embodiment, aliphatic hydrocarbon solvents are used as the solvent, such as isobutane, butane, pentane, isopentane, hexanes, isohexane, heptane, octane, dodecane, and mixtures thereof; cyclic and alicyclic hydrocarbons, such as cyclohexane, cycloheptane, methylcyclohexane, methylcycloheptane, and mixtures thereof. In another embodiment, the solvent is not aromatic, preferably aromatics are present in the solvent at less than 1 wt %, preferably less than 0.5 wt %, preferably less than 0 wt % based upon the weight of the solvents.

In a preferred embodiment, the feed concentration of the monomers and comonomers for the polymerization is 60 vol % solvent or less, preferably 40 vol % or less, or preferably 20 vol % or less, based on the total volume of the feedstream. Preferably the polymerization is run in a bulk process.

Preferred polymerizations can be run at any temperature and/or pressure suitable to obtain the desired ethylene polymers and as described above. Typical pressures include pressures in the range of from about 0.35 MPa to about 10 MPa, preferably from about 0.45 MPa to about 6 MPa, or preferably from about 0.5 MPa to about 4 MPa in some embodiments.

In some embodiments, hydrogen is present in the polymerization reactor at a partial pressure of 0.001 to 50 psig (0.007 to 345 kPa), preferably from 0.01 to 25 psig (0.07 to 172 kPa), more preferably 0.1 to 10 psig (0.7 to 70 kPa).

In a class of embodiments, the polymerization is performed in the gas phase, preferably, in a fluidized bed gas phase process. Generally, in a fluidized bed gas phase process used for producing polymers, a gaseous stream containing one or more monomers is continuously cycled through a fluidized bed in the presence of a catalyst under reactive conditions. The gaseous stream is withdrawn from the fluidized bed and recycled back into the reactor. Simultaneously, polymer product is withdrawn from the reactor and fresh monomer is added to replace the polymerized monomer. (See, for example, U.S. Pat. Nos. 4,543,399; 4,588,790; 5,028,670; 5,317,036; 5,352,749; 5,405,922; 5,436,304; 5,453,471; 5,462,999; 5,616,661; and 5,668,228; all of which are fully incorporated herein by reference.

In another embodiment of the invention, the polymerization is performed in the slurry phase. A slurry polymerization process generally operates between 1 to about 50 atmosphere pressure range (15 psi to 735 psi, 103 kPa to 5068 kPa) or even greater and temperatures as described above. In a slurry polymerization, a suspension of solid, particulate polymer is formed in a liquid polymerization diluent medium to which monomer and comonomers, along with catalysts, are added. The suspension including diluent is intermittently or continuously removed from the reactor where the volatile components are separated from the polymer and recycled, optionally after a distillation, to the reactor. The liquid diluent employed in the polymerization medium is typically an alkane having from 3 to 7 carbon atoms, preferably a branched alkane. The medium employed should be liquid under the conditions of polymerization and relatively inert. When a propane medium is used, the process is typically operated above the reaction diluent critical temperature and pressure. Often, a hexane or an isobutane medium is employed.

In an embodiment, a preferred polymerization technique useful in the invention is referred to as a particle form polymerization, or a slurry process where the temperature is kept below the temperature at which the polymer goes into solution. Such technique is known in the art, and described in for instance U.S. Pat. No. 3,248,179. A preferred temperature in the particle form process is within the range of about 85° C. to about 110° C. Two preferred polymerization methods for the slurry process are those employing a loop reactor and those utilizing a plurality of stirred reactors in series, parallel, or combinations thereof. Non-limiting examples of slurry processes include continuous loop or stirred tank processes. Also, other examples of slurry processes are described in U.S. Pat. No. 4,613,484, which is herein fully incorporated by reference.

In another embodiment, the slurry process is carried out continuously in a loop reactor. The catalyst, as a slurry in isobutane or as a dry free flowing powder, is injected regularly to the reactor loop, which is itself filled with circulating slurry of growing polymer particles in a diluent of isobutane containing monomer and comonomer. Hydrogen, optionally, may be added as a molecular weight control. In one embodiment 500 ppm or less of hydrogen is added, or 400 ppm or less or 300 ppm or less. In other embodiments at least 50 ppm of hydrogen is added, or 100 ppm or more, or 150 ppm or more.

Reaction heat is removed through the loop wall since much of the reactor is in the form of a double-jacketed pipe. The slurry is allowed to exit the reactor at regular intervals or continuously to a heated low pressure flash vessel, rotary dryer and a nitrogen purge column in sequence for removal of the isobutane diluent and all unreacted monomer and comonomers. The resulting hydrocarbon free powder is then compounded for use in various applications.

In a preferred embodiment, the catalyst system used in the polymerization comprises no more than one catalyst compound. A “reaction zone” also referred to as a “polymerization zone” is a vessel where polymerization takes place, for example a batch reactor. When multiple reactors are used in either series or parallel configuration, each reactor is considered as a separate polymerization zone. For a multi-stage polymerization in both a batch reactor and a continuous reactor, each polymerization stage is considered as a separate polymerization zone. In a preferred embodiment, the polymerization occurs in one reaction zone.

Useful reactor types and/or processes for the production of polyolefin polymers include, but are not limited to, UNIPOL™ Gas Phase Reactors (available from Univation Technologies); INEOS™ Gas Phase Reactors and Processes; Continuous Flow Stirred-Tank (CSTR) reactors (solution and slurry); Plug Flow Tubular reactors (solution and slurry); Slurry: (e.g., Slurry Loop (single or double loops)) (available from Chevron Phillips Chemical Company) and (Series Reactors) (available from Mitsui Chemicals)); BORSTAR™ Process and Reactors (slurry combined with gas phase); and Multi-Zone Circulating Reactors (MZCR) such as SPHERIZONE™ Reactors and Process available from Lyondell Basell.

In several classes of embodiments, the catalyst activity of the polymerization reaction is at least 4,250 g/g*cat or greater, at least 4,750 g/g*cat or greater, at least 5,000 g/g*cat or greater, at least 6,250 g/g*cat or greater, at least 8,500 g/g*cat or greater, at least 9,000 g/g*cat or greater, at least 9,500 g/g*cat or greater, or at least 9,700 g/g*cat or greater.

Polyolefin Products

In an embodiment, the process described herein produces polyethylene compositions including homopolymers and copolymers of one, two, three, four or more C₂ to C₄₀ olefin monomers, for example, C₂ to C₂₀ α-olefin monomers.

For example, the polyethyelene compositions include copolymers of a C₂ to C₄₀ olefin and one, two or three or more different C₂ to C₄₀ olefins, (where the C₂ to C₄₀ olefins are preferably C₃ to C₂₀ olefins, preferably are C₃ to C₁₂ α-olefin, preferably are propylene, butene, hexene, octene, decene, dodecene, preferably propylene, butene, hexene, octene, or a mixture thereof).

The polyethylene composition may comprise from 99.0 to about 80.0 wt %, 99.0 to 85.0 wt %, 99.0 to 87.5 wt %, 99.0 to 90.0 wt %, 99.0 to 92.5 wt %, 99.0 to 95.0 wt %, or 99.0 to 97.0 wt %, of polymer units derived from ethylene and about 1.0 to about 20.0 wt %, 1.0 to 15.0 wt %, 0.5 to 12.5 wt %, 1.0 to 10.0 wt %, 1.0 to 7.5 wt %, 1.0 to 5.0 wt %, or 1.0 to 3.0 wt % of polymer units derived from one or more C₃ to C₂₀ α-olefin comonomers, preferably C₃ to C₁₀ α-olefins, and more preferably C₄ to C₈ α-olefins, such as hexene and octene. The α-olefin comonomer may be linear or branched, and two or more comonomers may be used, if desired.

Examples of suitable comonomers include propylene, butene, 1-pentene; 1-pentene with one or more methyl, ethyl, or propyl substituents; 1-hexene; 1-hexene with one or more methyl, ethyl, or propyl substituents; 1-heptene; 1-heptene with one or more methyl, ethyl, or propyl substituents; 1-octene; 1-octene with one or more methyl, ethyl, or propyl substituents; 1-nonene; 1-nonene with one or more methyl, ethyl, or propyl substituents; ethyl, methyl, or dimethyl-substituted 1-decene; 1-dodecene; and styrene. Particularly suitable comonomers include 1-butene, 1-hexene, and 1-octene, 1-hexene, and mixtures thereof.

The polyethylene composition may have a melt index, I_(2.16), according to the test method listed below, of ≥about 0.10 g/10 min, e.g., ≥about 0.15 g/10 min, ≥about 0.18 g/10 min, ≥about 0.20 g/10 min, ≥about 0.22 g/10 min, ≥about 0.25 g/10 min, ≥about 0.28 g/10 min, or ≥about 0.30 g/10 min and, also, a melt index (I_(2.16))≤about 3.00 g/10 min, e.g., ≤about 2.00 g/10 min, ≤about 1.00 g/10 min, ≤about 0.70 g/10 min, ≤about 0.50 g/10 min, ≤about 0.40 g/10 min, or ≤about 0.30 g/10 min. Ranges expressly disclosed include, but are not limited to, ranges formed by combinations any of the above-enumerated values, e.g., about 0.10 to about 0.30, about 0.15 to about 0.25, about 0.18 to about 0.22 g/10 min, etc.

The polyethylene composition may have a high load melt index (HLMI) (I_(21.6)) in accordance with the test method listed below of from 1 to 60 g/10 min, 5 to 40 g/10 min, 15 to 40 g/10 min, or 18 to 39.5 g/10 min.

The polyethylene composition may have a melt index ratio (MIR), from 10 to 90, from 20 to 45, from 25 to 60, alternatively, from 30 to 55, alternatively, from 35 to 50, and alternatively, from 40 to 46. MIR is defined as I_(21.6)/I_(2.16).

The polyethylene composition may have a density of about 0.890 g/cm³, about 0.918 g/cm³≥about 0.920 g/cm³, e.g., ≥about 0.922 g/cm³, ≥about 0.928 g/cm³, ≥about 0.930 g/cm³, ≥about 0.932 g/cm³. Additionally, the polyethylene composition may have a density ≤about 0.945 g/cm³, e.g., ≤about 0.940 g/cm³, ≤about 0.937 g/cm³, ≤about 0.935 g/cm³, ≤about 0.933 g/cm³, or ≤about 0.930 g/cm³. Ranges expressly disclosed include, but are not limited to, ranges formed by combinations any of the above-enumerated values, e.g., about 0.920 to about 0.945 g/cm³, 0.920 to 0.930 g/cm³, 0.925 to 0.935 g/cm³, 0.920 to 0.940 g/cm³, etc. Density is determined in accordance with the test method listed below.

The polyethylene composition may have a molecular weight distribution (MWD, defined as M_(w)/M_(n)) of about 2 to about 12, about 5 to about 10.5 or 11, about 2.5 to about 5.5, preferably 4.0 to 5.0 and about 4.4 to 5.0.

In any of the embodiments described herein, the polyethylene composition may be a multimodal polyethylene composition such as a bimodal polyethylene composition. As used herein, “multimodal” means that there are at least two distinguishable peaks in a molecular weight distribution curve (as determined using gel permeation chromatography (GPC) or other recognized analytical technique) of a polyethylene composition. For example, if there are two distinguishable peaks in the molecular weight distribution curve such composition may be referred to as bimodal composition. Typically, if there is only one peak (e.g., monomodal), no obvious valley between the peaks, either one of the peaks is not considered as a distinguishable peak, or both peaks are not considered as distinguishable peaks, then such a composition may be referred to as non-bimodal. For example, in U.S. Pat. Nos. 8,846,841 and 8,691,715, FIGS. 1-5 illustrate representative bimodal molecular weight distribution curves. In these figures, there is a valley between the peaks, and the peaks can be separated or deconvoluted. Often, a bimodal molecular weight distribution is characterized as having an identifiable high molecular weight component (or distribution) and an identifiable low molecular weight component (or distribution). In contrast, in other embodiments, in U.S. Pat. Nos. 8,846,841 and 8,691,715, FIGS. 6-11 illustrate representative non-bimodal molecular weight distribution curves. These include unimodal molecular weight distributions as well as distribution curves containing two peaks that cannot be easily distinguished, separated, or deconvoluted.

In any of the embodiments described herein, the polyethylene composition may have an internal unsaturation as measured by ¹H NMR (see below for the test method) of less than 0.30 total internal unsaturations per thousand carbon atoms, less than 0.20 total internal unsaturations per thousand carbon atoms, less than 0.15 total internal unsaturations per thousand carbon atoms, or less than 0.10 total internal unsaturations per thousand carbon atoms.

In any of the embodiments described herein, the polyethylene composition may have a branching index a g′(vis) (see below for the test method) of 0.999 or less, 0.995 or less, 0.990 or less, 0.989 or less, or 0.988 or less.

Blends

In another embodiment, the polymer (preferably the polyethylene or polypropylene) or polyethylene composition produced herein is combined with one or more additional polymers in a blend prior to being formed into a film, molded part, or other article. As used herein, a “blend” may refer to a dry or extruder blend of two or more different polymers, and in-reactor blends, including blends arising from the use of multi or mixed catalyst systems in a single reactor zone, and blends that result from the use of one or more catalysts in one or more reactors under the same or different conditions (e.g., a blend resulting from in series reactors (the same or different) each running under different conditions and/or with different catalysts).

Useful additional polymers include other polyethylenes, isotactic polypropylene, highly isotactic polypropylene, syndiotactic polypropylene, random copolymer of propylene and ethylene, and/or butene, and/or hexene, polybutene, ethylene vinyl acetate, LDPE, LLDPE, HDPE, ethylene vinyl acetate, ethylene methyl acrylate, copolymers of acrylic acid, polymethylmethacrylate or any other polymers polymerizable by a high-pressure free radical process, polyvinylchloride, polybutene-1, isotactic polybutene, ABS resins, ethylene-propylene rubber (EPR), vulcanized EPR, EPDM, block copolymer, styrenic block copolymers, polyamides, polycarbonates, PET resins, cross linked polyethylene, copolymers of ethylene and vinyl alcohol (EVOH), polymers of aromatic monomers such as polystyrene, poly-1 esters, polyacetal, polyvinylidine fluoride, polyethylene glycols, and/or polyisobutylene.

End Uses

Any of the foregoing polymers and compositions in combination with optional additives (see, for example, U.S. Publication No. 2016/0060430, paragraphs [0082]-[0093]) may be used in a variety of end-use applications. Such end uses may be produced by methods known in the art. End uses include polymer products and products having specific end-uses. Exemplary end uses are films, film-based products, diaper backsheets, housewrap, wire and cable coating compositions, articles formed by molding techniques, e.g., injection or blow molding, extrusion coating, foaming, casting, and combinations thereof. End uses also include products made from films, e.g., bags, packaging, and personal care films, pouches, medical products, such as for example, medical films and intravenous (IV) bags.

Films

Films include monolayer or multilayer films. Films include those film structures and film applications known to those skilled in the art. Specific end use films include, for example, blown films, cast films, stretch films, stretch/cast films, stretch cling films, stretch hand wrap films, machine stretch wrap, shrink films, shrink wrap films, green house films, laminates, and laminate films. Exemplary films are prepared by any conventional technique known to those skilled in the art, such as for example, techniques utilized to prepare blown, extruded, and/or cast stretch and/or shrink films (including shrink-on-shrink applications).

In one embodiment, multilayer films or multiple-layer films may be formed by methods well known in the art. The total thickness of multilayer films may vary based upon the application desired. A total film thickness of about 5-100 μm, more typically about 10-50 μm, is suitable for most applications. Those skilled in the art will appreciate that the thickness of individual layers for multilayer films may be adjusted based on desired end-use performance, resin or copolymer employed, equipment capability, and other factors. The materials forming each layer may be coextruded through a coextrusion feedblock and die assembly to yield a film with two or more layers adhered together but differing in composition. Coextrusion can be adapted for use in both cast film or blown film processes. Exemplary multilayer films have at least two, at least three, or at least four layers. In one embodiment the multilayer films are composed of five to ten layers.

To facilitate discussion of different film structures, the following notation is used herein. Each layer of a film is denoted “A” or “B”. Where a film includes more than one A layer or more than one B layer, one or more prime symbols (′, ″, ′″, etc.) are appended to the A or B symbol to indicate layers of the same type that can be the same or can differ in one or more properties, such as chemical composition, density, melt index, thickness, etc. Finally, the symbols for adjacent layers are separated by a slash (/). Using this notation, a three-layer film having an inner layer disposed between two outer layers would be denoted A/B/A′. Similarly, a five-layer film of alternating layers would be denoted A/B/A′/B′/A″. Unless otherwise indicated, the left-to-right or right-to-left order of layers does not matter, nor does the order of prime symbols; e.g., an A/B film is equivalent to a B/A film, and an A/A′/B/A″ film is equivalent to an A/B/A′/A″ film, for purposes described herein. The relative thickness of each film layer is similarly denoted, with the thickness of each layer relative to a total film thickness of 100 (dimensionless) indicated numerically and separated by slashes; e.g., the relative thickness of an A/B/A′ film having A and A′ layers of 10 μm each and a B layer of 30 μm is denoted as 20/60/20.

The thickness of each layer of the film, and of the overall film, is not particularly limited, but is determined according to the desired properties of the film. Typical film layers have a thickness of from about 1 to about 1000 μm, more typically from about 5 to about 100 μm, and typical films have an overall thickness of from about 10 to about 100 μm.

In some embodiments, and using the nomenclature described above, the present invention provides for multilayer films with any of the following exemplary structures: (a) two-layer films, such as A/B and B/B′; (b) three-layer films, such as A/B/A′, A/A′/B, B/A/B′ and B/B′/B″; (c) four-layer films, such as A/A′/A″/B, A/A′/B/A″, A/A′/B/B′, A/B/A′/B′, A/B/B′/A′, B/A/A′/B′, A/B/B′/B″, B/A/B′/B″ and B/B′/B″/B′″; (d) five-layer films, such as A/A′/A″/A′″/B, A/A′/A″/B/A′″, A/A′/B/A″/A′″, A/A′/A″/B/B′, A/A′/B/A″/B′, A/A′/B/B′/A″, A/B/A′/B′/A″, A/B/A′/A″/B, B/A/A′/A″/B′, A/A′/B/B′/B″, A/B/A′/B′/B″, A/B/B′/B″/A′, B/A/A′/B′/B″, B/A/B′/A′/B″, B/A/B′/B″/A′, A/B/B′/B″/B′″, B/A/B′/B″/B′″, B/B′/A/B″/B′″, and B/B′/B″/B′″/B″″; and similar structures for films having six, seven, eight, nine, twenty-four, forty-eight, sixty-four, one hundred, or any other number of layers. It should be appreciated that films having still more layers.

In any of the embodiments above, one or more A layers can be replaced with a substrate layer, such as glass, plastic, paper, metal, etc., or the entire film can be coated or laminated onto a substrate. Thus, although the discussion herein has focused on multilayer films, the films may also be used as coatings for substrates such as paper, metal, glass, plastic, and other materials capable of accepting a coating.

The films can further be embossed, or produced or processed according to other known film processes. The films can be tailored to specific applications by adjusting the thickness, materials and order of the various layers, as well as the additives in or modifiers applied to each layer.

In a class of embodiments, a film (e.g., blown or cast) made from the polyethylene composition as described above, may a have:

i) a relationship between MD/TD modulus (in accordance with the test method described below) and density that satisfies the following equation: Avg. Modulus≥1.2*(Constant 1(C1)*Density−Constant 2(C2); and

ii) a seal initiation temperature (in accordance with the test method described below) at 1 N of ≤98.0° C.

For example, the relationship between MD/TD modulus and density may be as follows: Average Modulus≥1.2*(2,065,292*Density−1,872,345).

In any of the embodiments described herein, the seal initiation temperature (see below for the test method) at 1 N may be ≤99.0° C., ≤98.0° C., ≤97.0° C., ≤96.0° C., ≤95.0° C., or ≤94.0° C.

In any of the embodiments described herein, the seal initiation temperature (see below for the test method) at 5 N is ≤103.0° C., ≤102.0° C., ≤101.0° C., ≤100.0° C., ≤99.0° C., or ≤98.0° C.

In any of the embodiments described herein, the film may exhibit an average 1% secant MD/TD modulus (see below for the test method) of 30,000 psi or greater, an average 1% secant MD/TD modulus of 35,000 psi or greater, an average 1% secant MD/TD modulus of 40,000 psi or greater, an average 1% secant MD/TD modulus of 45,000 psi or greater, or an average 1% secant MD/TD modulus of 50,000 psi or greater.

Stretch Films

The polymers and compositions as described above may be utilized to prepare stretch films. Stretch films are widely used in a variety of bundling and packaging applications. The term “stretch film” indicates films capable of stretching and applying a bundling force, and includes films stretched at the time of application as well as “pre-stretched” films, i.e., films which are provided in a pre-stretched form for use without additional stretching. Stretch films can be monolayer films or multilayer films, and can include conventional additives, such as cling-enhancing additives such as tackifiers, and non-cling or slip additives, to tailor the slip/cling properties of the film.

Shrink Films

The polymers and compositions as described above may be utilized to prepare shrink films. Shrink films, also referred to as heat-shrinkable films, are widely used in both industrial and retail bundling and packaging applications. Such films are capable of shrinking upon application of heat to release stress imparted to the film during or subsequent to extrusion. The shrinkage can occur in one direction or in both longitudinal and transverse directions. Conventional shrink films are described, for example, in WO 2004/022646.

Industrial shrink films are commonly used for bundling articles on pallets. Typical industrial shrink films are formed in a single bubble blown extrusion process to a thickness of about 80 to 200 μm, and provide shrinkage in two directions, typically at a machine direction (MD) to transverse direction (TD) ratio of about 60:40.

Retail films are commonly used for packaging and/or bundling articles for consumer use, such as, for example, in supermarket goods. Such films are typically formed in a single bubble blown extrusion process to a thickness of about 35 to 80, μm, with a typical MD:TD shrink ratio of about 80:20.

Films may be used in “shrink-on-shrink” applications. “Shrink-on-shrink,” as used herein, refers to the process of applying an outer shrink wrap layer around one or more items that have already been individually shrink wrapped (herein, the “inner layer” of wrapping). In these processes, it is desired that the films used for wrapping the individual items have a higher melting (or shrinking) point than the film used for the outside layer. When such a configuration is used, it is possible to achieve the desired level of shrinking in the outer layer, while preventing the inner layer from melting, further shrinking, or otherwise distorting during shrinking of the outer layer. Some films described herein have been observed to have a sharp shrinking point when subjected to heat from a heat gun at a high heat setting, which indicates that they may be especially suited for use as the inner layer in a variety of shrink-on-shrink applications.

Greenhouse Films

The polymers and compositions as described above may be utilized to prepare stretch to prepare greenhouse films. Greenhouse films are generally heat retention films that, depending on climate requirements, retain different amounts of heat. Less demanding heat retention films are used in warmer regions or for spring time applications. More demanding heat retention films are used in the winter months and in colder regions.

Bags

Bags include those bag structures and bag applications known to those skilled in the art. Exemplary bags include shipping sacks, trash bags and liners, industrial liners, produce bags, and heavy duty bags.

Packaging

Packaging includes those packaging structures and packaging applications known to those skilled in the art. Exemplary packaging includes flexible packaging, food packaging, e.g., fresh cut produce packaging, frozen food packaging, bundling, packaging and unitizing a variety of products. Applications for such packaging include various foodstuffs, rolls of carpet, liquid containers, and various like goods normally containerized and/or palletized for shipping, storage, and/or display.

Blow Molded Articles

The polymers and compositions described above may also be used in blow molding processes and applications. Such processes are well known in the art, and involve a process of inflating a hot, hollow thermoplastic preform (or parison) inside a closed mold. In this manner, the shape of the parison conforms to that of the mold cavity, enabling the production of a wide variety of hollow parts and containers.

In a typical blow molding process, a parison is formed between mold halves and the mold is closed around the parison, sealing one end of the parison and closing the parison around a mandrel at the other end. Air is then blown through the mandrel (or through a needle) to inflate the parison inside the mold. The mold is then cooled and the part formed inside the mold is solidified. Finally, the mold is opened and the molded part is ejected. The process lends itself to any design having a hollow shape, including but not limited to bottles, tanks, toys, household goods, automobile parts, and other hollow containers and/or parts.

Blow molding processes may include extrusion and/or injection blow molding. Extrusion blow molding is typically suited for the formation of items having a comparatively heavy weight, such as greater than about 12 ounces, including but not limited to food, laundry, or waste containers. Injection blow molding is typically used to achieve accurate and uniform wall thickness, high quality neck finish, and to process polymers that cannot be extruded. Typical injection blow molding applications include, but are not limited to, pharmaceutical, cosmetic, and single serving containers, typically weighing less than 12 ounces.

Injection Molded Articles

The polymers and compositions described above may also be used in injection molded applications. Injection molding is a process commonly known in the art, and is a process that usually occurs in a cyclical fashion. Cycle times generally range from 10 to 100 seconds and are controlled by the cooling time of the polymer or polymer blend used.

In a typical injection molding cycle, polymer pellets or powder are fed from a hopper and melted in a reciprocating screw type injection molding machine. The screw in the machine rotates forward, filling a mold with melt and holding the melt under high pressure. As the melt cools in the mold and contracts, the machine adds more melt to the mold to compensate. Once the mold is filled, it is isolated from the injection unit and the melt cools and solidifies. The solidified part is ejected from the mold and the mold is then closed to prepare for the next injection of melt from the injection unit.

Injection molding processes offer high production rates, good repeatability, minimum scrap losses, and little to no need for finishing of parts. Injection molding is suitable for a wide variety of applications, including containers, household goods, automobile components, electronic parts, and many other solid articles.

Extrusion Coating

The polymers and compositions described above may be used in extrusion coating processes and applications. Extrusion coating is a plastic fabrication process in which molten polymer is extruded and applied onto a non-plastic support or substrate, such as paper or aluminum in order to obtain a multi-material complex structure. This complex structure typically combines toughness, sealing and resistance properties of the polymer formulation with barrier, stiffness or aesthetics attributes of the non-polymer substrate. In this process, the substrate is typically fed from a roll into a molten polymer as the polymer is extruded from a slot die, which is similar to a cast film process. The resultant structure is cooled, typically with a chill roll or rolls, and would into finished rolls.

Extrusion coating materials are typically used in food and non-food packaging, pharmaceutical packaging, and manufacturing of goods for the construction (insulation elements) and photographic industries (paper).

Foamed Articles

The polymers and compositions described above may be used in foamed applications. In an extrusion foaming process, a blowing agent, such as, for example, carbon dioxide, nitrogen, or a compound that decomposes to form carbon dioxide or nitrogen, is injected into a polymer melt by means of a metering unit. The blowing agent is then dissolved in the polymer in an extruder, and pressure is maintained throughout the extruder. A rapid pressure drop rate upon exiting the extruder creates a foamed polymer having a homogenous cell structure. The resulting foamed product is typically light, strong, and suitable for use in a wide range of applications in industries such as packaging, automotive, aerospace, transportation, electric and electronics, and manufacturing.

Wire and Cable Applications

Also provided are electrical articles and devices including one or more layers formed of or comprising the polymers and compositions described above. Such devices include, for example, electronic cables, computer and computer-related equipment, marine cables, power cables, telecommunications cables or data transmission cables, and combined power/telecommunications cables.

Electrical devices described herein can be formed by methods well known in the art, such as by one or more extrusion coating steps in a reactor/extruder equipped with a cable die. Such cable extrusion apparatus and processes are well known. In a typical extrusion method, an optionally heated conducting core is pulled through a heated extrusion die, typically a cross-head die, in which a layer of melted polymer composition is applied. Multiple layers can be applied by consecutive extrusion steps in which additional layers are added, or, with the proper type of die, multiple layers can be added simultaneously. The cable can be placed in a moisture curing environment, or allowed to cure under ambient conditions.

Test Methods

¹H NMR

¹H NMR data was collected at 393K in a 10 mm probe using a Bruker spectrometer with a ¹H frequency of 400 MHz (available from Agilent Technologies, Santa Clara, Calif.). Data was recorded using a maximum pulse width of 45° C., 5 seconds between pulses and signal averaging 512 transients. Spectral signals were integrated and the number of unsaturation types per 1000 carbons was calculated by multiplying the different groups by 1000 and dividing the result by the total number of carbons. M_(n) was calculated by dividing the total number of unsaturated species into 14,000, and has units of g/mol.

TREF Method

Unless otherwise indicated, the TREF-LS data reported herein were measured using an analytical size TREF instrument (Polymerchar, Spain), with a column of the following dimension: inner diameter (ID) 7.8 mm and outer diameter (OD) 9.53 mm and a column length of 150 mm. The column was filled with steel beads. 0.5 mL of a 6.4% (w/v) polymer solution in orthodichlorobenzene (ODCB) containing 6 g BHT/4 L were charged onto the column and cooled from 140° C. to 25° C. at a constant cooling rate of 1.0° C./min. Subsequently, the ODCB was pumped through the column at a flow rate of 1.0 ml/min and the column temperature was increased at a constant heating rate of 2° C./min to elute the polymer. The polymer concentration in the eluted liquid was detected by means of measuring the absorption at a wavenumber of 2857 cm¹ using an infrared detector. The concentration of the ethylene-α-olefin copolymer in the eluted liquid was calculated from the absorption and plotted as a function of temperature. The molecular weight of the ethylene-α-olefin copolymer in the eluted liquid was measured by light scattering using a Minidawn Tristar light scattering detector (Wyatt, Calif., USA). The molecular weight was also plotted as a function of temperature.

GPC 4D Procedure: Molecular Weight, Comonomer Composition and Long Chain Branching Determination by GPC-IR Hyphenated with Multiple Detectors

The distribution and the moments of molecular weight (M_(w), M_(n), M_(w)/M_(n), etc.), the comonomer content (C₂, C₃, C₆, etc.) and the branching index (g′vis) are determined by using a high temperature Gel Permeation Chromatography (Polymer Char GPC-IR) equipped with a multiple-channel band-filter based Infrared detector IR5, an 18-angle light scattering detector and a viscometer. Three Agilent PLgel 10-μm Mixed-B LS columns are used to provide polymer separation. Aldrich reagent grade 1,2,4-trichlorobenzene (TCB) with 300 ppm antioxidant butylated hydroxytoluene (BHT) is used as the mobile phase. The TCB mixture is filtered through a 0.1 μm Teflon filter and degassed with an online degasser before entering the GPC instrument. The nominal flow rate is 1.0 ml/min and the nominal injection volume is 200 μL. The whole system including transfer lines, columns, and detectors are contained in an oven maintained at 145° C. The polymer sample is weighed and sealed in a standard vial with 80 μL flow marker (Heptane) added to it. After loading the vial in the autosampler, polymer is automatically dissolved in the instrument with 8 ml added TCB solvent. The polymer is dissolved at 160° C. with continuous shaking for about 1 hour for PE samples or 2 hour for PP samples. The TCB densities used in concentration calculation are 1.463 g/ml at about 23° C. temperature and 1.284 g/ml at 145° C. The sample solution concentration is from 0.2 to 2.0 mg/ml, with lower concentrations being used for higher molecular weight samples. The concentration (c), at each point in the chromatogram is calculated from the baseline-subtracted IR5 broadband signal intensity (I), using the following equation: c=βI, where β is the mass constant. The mass recovery is calculated from the ratio of the integrated area of the concentration chromatography over elution volume and the injection mass which is equal to the pre-determined concentration multiplied by injection loop volume. The conventional molecular weight (IR MW) is determined by combining universal calibration relationship with the column calibration which is performed with a series of monodispersed polystyrene (PS) standards ranging from 700 to 10M gm/mole. The MW at each elution volume is calculated with following equation:

${{\log\; M} = {\frac{\log\left( {K_{PS}/K} \right)}{a + 1} + {\frac{a_{PS} + 1}{a + 1}\log\; M_{PS}}}},$ where the variables with subscript “PS” stand for polystyrene while those without a subscript are for the test samples. In this method, α_(PS)=0.67 and K_(PS)=0.000175 while a and K are for other materials as calculated and published in literature (Sun, T. et al. Macromolecules 2001, 34, 6812), except that for purposes of this invention and claims thereto, α=0.695 and K=0.000579 for linear ethylene polymers, α=0.705 and K=0.0002288 for linear propylene polymers, α=0.695 and K=0.000181 for linear butene polymers, a is 0.695 and K is 0.000579*(1−0.0087*w2b+0.000018*(w2b){circumflex over ( )}2) for ethylene-butene copolymer where w2b is a bulk weight percent of butene comonomer, α is 0.695 and K is 0.000579*(1−0.0075*w2b) for ethylene-hexene copolymer where w2b is a bulk weight percent of hexene comonomer, and α is 0.695 and K is 0.000579*(1−0.0077*w2b) for ethylene-octene copolymer where w2b is a bulk weight percent of octene comonomer. Concentrations are expressed in g/cm³, molecular weight is expressed in g/mole, and intrinsic viscosity (hence K in the Mark-Houwink equation) is expressed in dL/g unless otherwise noted.

The comonomer composition is determined by the ratio of the IR5 detector intensity corresponding to CH₂ and CH₃ channel calibrated with a series of PE and PP homo/copolymer standards whose nominal value are predetermined by NMR or FTIR. In particular, this provides the methyls per 1000 total carbons (CH₃/1000TC) as a function of molecular weight. The short-chain branch (SCB) content per 1000TC (SCB/1000TC) is then computed as a function of molecular weight by applying a chain-end correction to the CH₃/1000TC function, assuming each chain to be linear and terminated by a methyl group at each end. The wt % comonomer is then obtained from the following expression in which f is 0.3, 0.4, 0.6, 0.8, and so on for C₃, C₄, C₆, C₈, and so on co-monomers, respectively: w2=f*SCB/1000TC.

The bulk composition of the polymer from the GPC-IR and GPC-4D analyses is obtained by considering the entire signals of the CH₃ and CH₂ channels between the integration limits of the concentration chromatogram. First, the following ratio is obtained

${{Bulk}\mspace{14mu}{IR}\mspace{14mu}{ratio}} = {\frac{{Area}\mspace{14mu}{of}\mspace{14mu}{CH}_{3}\mspace{11mu}{signal}{\mspace{11mu}\;}{within}\mspace{14mu}{integration}\mspace{14mu}{limits}}{{Area}\mspace{14mu}{of}\mspace{14mu}{CH}_{2}\mspace{11mu}{signal}\mspace{14mu}{within}\mspace{14mu}{integration}\mspace{14mu}{limits}}.}$

Then the same calibration of the CH₃ and CH₂ signal ratio, as mentioned previously in obtaining the CH3/1000TC as a function of molecular weight, is applied to obtain the bulk CH3/1000TC. A bulk methyl chain ends per 1000TC (bulk CH3end/1000TC) is obtained by weight-averaging the chain-end correction over the molecular-weight range. Then w2b=f*bulk CH3/1000TC bulk SCB/1000TC=bulk CH3/1000TC−bulk CH3end/1000TC and bulk SCB/1000TC is converted to bulk w2 in the same manner as described above.

The LS detector is the 18-angle Wyatt Technology High Temperature DAWN HELEOSII. The LS molecular weight (M) at each point in the chromatogram is determined by analyzing the LS output using the Zimm model for static light scattering (Light Scattering from Polymer Solutions; Huglin, M. B., Ed.; Academic Press, 1972.):

$\frac{K_{o}c}{\Delta\;{R(\theta)}} = {\frac{1}{{MP}(\theta)} + {2A_{2}{c.}}}$

Here, ΔR(θ) is the measured excess Rayleigh scattering intensity at scattering angle θ, c is the polymer concentration determined from the IR5 analysis, A2 is the second virial coefficient, P(θ) is the form factor for a monodisperse random coil, and K_(O) is the optical constant for the system:

${K_{o} = \frac{4\;\pi^{2}{n^{2}\left( {{dn}/{dc}} \right)}^{2}}{\lambda^{4}N_{A}}},$ where NA is Avogadro's number, and (dn/dc) is the refractive index increment for the system. The refractive index, n=1.500 for TCB at 145° C. and λ=665 nm. For analyzing polyethylene homopolymers, ethylene-hexene copolymers, and ethylene-octene copolymers, dn/dc=0.1048 ml/mg and A2=0.0015; for analyzing ethylene-butene copolymers, dn/dc=0.1048*(1−0.00126*w2) ml/mg and A2=0.0015 where w2 is weight percent butene comonomer.

A high temperature Agilent (or Viscotek Corporation) viscometer, which has four capillaries arranged in a Wheatstone bridge configuration with two pressure transducers, is used to determine specific viscosity. One transducer measures the total pressure drop across the detector, and the other, positioned between the two sides of the bridge, measures a differential pressure. The specific viscosity, is, for the solution flowing through the viscometer is calculated from their outputs. The intrinsic viscosity, [η], at each point in the chromatogram is calculated from the equation [η]=ηs/c, where c is concentration and is determined from the IR5 broadband channel output. The viscosity MW at each point is calculated as M=K_(PS)M^(α) ^(PS) ⁺¹/[η] where α_(PS) is 0.67 and K_(PS) is 0.000175.

The branching index (g′vis) is calculated using the output of the GPC-IR5-LS-VIS method as follows. The average intrinsic viscosity, [η]avg, of the sample is calculated by:

${\lbrack\eta\rbrack_{avg} = \frac{\sum{c_{i}\lbrack\eta\rbrack}_{i}}{\sum c_{i}}},$ where the summations are over the chromatographic slices, i, between the integration limits. The branching index g′vis is defined as

${g_{vis}^{\prime} = \frac{\lbrack\eta\rbrack_{avg}}{{KM}_{v}^{\alpha}}},$ where My is the viscosity-average molecular weight based on molecular weights determined by LS analysis and the K and α are for the reference linear polymer, which are, for purposes of this invention and claims thereto, α=0.695 and K=0.000579 for linear ethylene polymers, α=0.705 and K=0.0002288 for linear propylene polymers, α=0.695 and K=0.000181 for linear butene polymers, α is 0.695 and K is 0.000579*(1−0.0087*w2b+0.000018*(w2b){circumflex over ( )}2) for ethylene-butene copolymer where w2b is a bulk weight percent of butene comonomer, α is 0.695 and K is 0.000579*(1−0.0075*w2b) for ethylene-hexene copolymer where w2b is a bulk weight percent of hexene comonomer, and α is 0.695 and K is 0.000579*(1−0.0077*w2b) for ethylene-octene copolymer where w2b is a bulk weight percent of octene comonomer. Concentrations are expressed in g/cm³, molecular weight is expressed in g/mole, and intrinsic viscosity (hence K in the Mark-Houwink equation) is expressed in dL/g unless otherwise noted. Calculation of the w2b values is as discussed above.

The reversed-co-monomer index (RCI,m) is computed from x2 (mol % co-monomer C₃, C₄, C₆, C₈, etc.), as a function of molecular weight, where x2 is obtained from the following expression in which n is the number of carbon atoms in the comonomer (3 for C₃, 4 for C₄, 6 for C₆, etc.):

${x\; 2} = {- {\frac{200\mspace{14mu} w\; 2}{{{- 100}\mspace{14mu} n} - {2\mspace{14mu} w\; 2} + {n\mspace{14mu} w\; 2}}.}}$

Then the molecular-weight distribution, W(z) where z=log₁₀ M, is modified to W′(z) by setting to 0 the points in W that are less than 5% of the maximum of W; this is to effectively remove points for which the S/N in the composition signal is low. Also, points of W′ for molecular weights below 2000 gm/mole are set to 0. Then W′ is renormalized so that 1=∫_(−∞) ^(∞)W′dz, and a modified weight-average molecular weight (M_(w)′) is calculated over the effectively reduced range of molecular weights as follows: M_(w)′=∫_(−∞) ^(∞)10^(z)*W′dz.

The RCI,m is then computed as RCI,m=∫ _(−∞) ^(∞) x2(10^(z)−M_(w)′)W′dz.

A reversed-co-monomer index (RCI,w) is also defined on the basis of the weight fraction co-monomer signal (w2/100) and is computed as follows:

${RCI},{w = {\int_{- \infty}^{\infty}{\frac{w\; 2}{100}\left( {10^{z} - M_{w}^{\prime}} \right)W^{\prime}{{dz}.}}}}$

In the above definite integrals the limits of integration are the widest possible for the sake of generality; however, in reality the function is only integrated over a finite range for which data is acquired, considering the function in the rest of the non-acquired range to be 0. Also, by the manner in which W′ is obtained, it is possible that W′ is a discontinuous function, and the above integrations need to be done piecewise.

Three co-monomer distribution ratios are also defined on the basis of the % weight (w2) comonomer signal, denoted as CDR-1,w, CDR-2,w, and CDR-3,w, as follows:

${{CDR}\text{-}1},{w = \frac{w\; 2({Mz})}{w\; 2({Mw})}},{{CDR}\text{-}2},{w = \frac{w\; 2({Mz})}{w\; 2\left( \frac{{Mw} + {Mn}}{2} \right)}},{{CDR}\text{-}3},{w = \frac{w\; 2\left( \frac{{Mz} + {Mw}}{2} \right)}{w\; 2\left( \frac{{Mw} + {Mn}}{2} \right)}},$ where w2(Mw) is the % weight co-monomer signal corresponding to a molecular weight of Mw, w2(Mz) is the % weight co-monomer signal corresponding to a molecular weight of Mz, w2[(Mw+Mn)/2)] is the % weight co-monomer signal corresponding to a molecular weight of (Mw+Mn)/2, and w2[(Mz+Mw)/2] is the % weight co-monomer signal corresponding to a molecular weight of Mz+Mw/2, where Mw is the weight-average molecular weight, Mn is the number-average molecular weight, and Mz is the z-average molecular weight.

Accordingly, the co-monomer distribution ratios can be also defined utilizing the % mole co-monomer signal, CDR-1,m, CDR-2,m, CDR-3,m, as

${{CDR}\text{-}1},{m = \frac{x\; 2({Mz})}{x\; 2({Mw})}},{{CDR}\text{-}2},{m = \frac{x\; 2({Mz})}{x\; 2\left( \frac{{MW} + {Mn}}{2} \right)}},{{CDR}\text{-3}},{m = \frac{x\; 2\left( \frac{{Mz} + {Mw}}{2} \right)}{x\; 2\left( \frac{{Mw} + {Mn}}{2} \right)}},$ where x2(Mw) is the % mole co-monomer signal corresponding to a molecular weight of Mw, x2(Mz) is the % mole co-monomer signal corresponding to a molecular weight of Mz, x2[(Mw+Mn)/2)] is the % mole co-monomer signal corresponding to a molecular weight of (Mw+Mn)/2, and x2[(Mz+Mw)/2] is the % mole co-monomer signal corresponding to a molecular weight of Mz+Mw/2, where Mw is the weight-average molecular weight, Mn is the number-average molecular weight, and Mz is the z-average molecular weight. Cross-Fractionation Chromatography (CFC)

Cross-fractionation chromatography (CFC) analysis was done using a CFC-2 instrument from Polymer Char, S.A., Valencia, Spain. The principles of CFC analysis and a general description of the particular apparatus used are given in the article by Ortin, A.; Monrabal, B.; Sancho-Tello, 257 J. Macromol. Symp. 13 (2007). In FIG. 1 of the article is an appropriate schematic of the particular apparatus used. Details of the analysis method and features of the apparatus used are as follows.

The solvent used for preparing the sample solution and for elution was 1,2-Dichlorobenzene (ODCB) which was stabilized by dissolving 2 g of 2,6-bis(1,1-dimethylethyl)-4-methylphenol (butylated hydroxytoluene) in a 4-L bottle of fresh solvent at ambient temperature. The sample to be analyzed (25-125 mg) was dissolved in the solvent (25 ml metered at ambient temperature) by stirring (200 rpm) at 150° C. for 75 min. A small volume (0.5 ml) of the solution was introduced into a TREF column (stainless steel; o.d., ⅜″; length, 15 cm; packing, non-porous stainless steel micro-balls) at 150° C., and the column temperature was stabilized for 30 min at a temperature (120-125° C.) approximately 20° C. higher than the highest-temperature fraction for which the GPC analysis was included in obtaining the final bivariate distribution. The sample volume was then allowed to crystallize in the column by reducing the temperature to an appropriate low temperature (30, 0, or −15° C.) at a cooling rate of 0.2° C./min. The low temperature was held for 10 min before injecting the solvent flow (1 ml/min) into the TREF column to elute the soluble fraction (SF) into the GPC columns (3×PLgel 10 μm Mixed-B 300×7.5 mm, Agilent Technologies, Inc.); the GPC oven was held at high temperature (140° C.). The SF was eluted for 5 min from the TREF column and then the injection valve was put in the “load” position for 40 min to completely elute all of the SF through the GPC columns (standard GPC injections). All subsequent higher-temperature fractions were analyzed using overlapped GPC injections wherein at each temperature step the polymer was allowed to dissolve for at least 16 min and then eluted from the TREF column into the GPC column for 3 min. The IR4 (Polymer Char) infrared detector was used to generate an absorbance signal that is proportional to the concentration of polymer in the eluting flow.

The universal calibration method was used for determining the molecular weight distribution (MWD) and molecular-weight averages (M_(n), M_(w), etc.) of eluting polymer fractions. Thirteen narrow molecular-weight distribution polystyrene standards (obtained from Agilent Technologies, Inc.) within the range of 1.5-8200 kg/mol were used to generate a universal calibration curve. Mark-Houwink parameters were obtained from Appendix I of Mori, S.; Barth, H. G. Size Exclusion Chromatography; Springer, 1999. For polystyrene K=1.38×10⁻⁴ dl/g and α=0.7; and for polyethylene K=5.05×10⁻⁴ dl/g and α=0.693 were used. For a polymer fraction, which eluted at a temperature step, that has a weight fraction (wt % recovery) of less than 0.5%, the MWD and the molecular-weight averages were not computed; additionally, such polymer fractions were not included in computing the MWD and the molecular-weight averages of aggregates of fractions.

Measuring Tw1, Tw2, Mw1 and Mw2 from CFC

A technique has been developed for determining both MWD and SCBD compositional information, using cryogenic cross fractionation (cryo CFC), to compare the polymers. The procedures for the determination of CFC data are discussed in more detail below.

In the section of “Fraction summary” in the CFC data file, each fraction is listed by its fractionation temperature (Ti) along with its normalized wt % value (Wi), cumulative wt %, i.e., Sum wt. on FIG. 1 and FIG. 2, and various moments of molecular weight averages (including weight average molecular weight, Mwi).

FIG. 1 and FIG. 2 are plots that graphically illustrate the calculations used to determine the CFC result. Only fractions having MWD data are considered. In both FIG. 1 and FIG. 2, the x-axis represents the elution temperature in centigrade, while the right hand y-axis represents the value of the integral of the weights of polymer that have been eluted up to an elution temperature. The temperature at which 100% of the material has eluted in this example is about 100° C. The closest point at which 50% of the polymer has eluted is determined by the integral, which is used then to divide each of the plots into a 1^(st)-half and a 2^(nd)-half.

To calculate values of Tw1, Tw2, Mw1 and Mw2, the data in “Fraction summary” was divided into two roughly equal halves. Weight averages of Ti and Mwi; for each half were calculated according to the conventional definition of weight average. Fractions which did not have sufficient quantity (i.e., <0.5 wt %) to be processed for molecular weight averages in the original data file were excluded from the calculation of Tw1, Tw2, Mw1 and M_(w)2.

The first part of the process is illustrated by FIG. 1. From the section of fraction summary in the CFC data file, the fraction whose cumulative wt % (i.e., Sum wt) is closest to 50 is identified (e.g., the fraction at 84° C. on FIG. 1). The Fraction summary data is divided into two halves, e.g., Ti<=84° C. as the 1st half and Ti>84° C. as the 2nd half on FIG. 1. Fractions which do not have molecular weight averages reported in the original data file are excluded, e.g., excluding the fractions with Ti between 25° C. and 40° C. on FIG. 1.

In FIG. 1, the left hand y-axis represents the wt % of the eluted fraction. Using the procedure above to divide the curves into two halves, these values are used to calculate the weight average elution temperature for each half using the formula shown in Eqn. 1.

$\begin{matrix} {{Tw} = \frac{\sum{TiWi}}{\sum{Wi}}} & {{Eqn}.\mspace{14mu} 1} \end{matrix}$

In Eqn. 1, Ti represents the elution temperature for each eluted fraction, and Wi represents the normalized wt % (polymer amount) of each eluted fraction. For the example shown in FIG. 2, this provides a weight average elution temperature of 64.9° C. for the first half, and 91.7° C. for the second half.

In FIG. 2, the left hand axis represents the weight average molecular weight (Mwj) of each eluted fraction. These values are used to calculate the weight average molecular weight for each half using the formula shown in Eqn. 2.

$\begin{matrix} {{Mw} = \frac{\sum{MwiWi}}{\sum{Wi}}} & {{Eqn}.\mspace{14mu} 2} \end{matrix}$

In Eqn. 2, Mw; represents the weight average molecular weight of each eluted fraction, and Wj represents the normalized wt % (polymer amount) of each eluted fraction. For the example shown in FIG. 2, this provides a weight average molecular weight of 237,539 g/mole for the first half, and 74,156 g/mole for the second half. The values calculated using the techniques described above may be used to classify the MWD×SCBD for experimental polymers and control polymers.

FIG. 3 is a semi-log plot of (Mw1/Mw2) vs. (Tw1-Tw2) designed to show the important differences in MWD/SCBD combination among inventive examples vs. commercial benchmarks. Such differences are believed to play a key role in determining the trade-off pattern and/or balance of various performance attributes such as stiffness, toughness and processability.

In the plot FIG. 3, the x-axis represents the value of the difference between the first and second weight average elution temperatures (Tw1-Tw2). The y-axis in a log scale represents the ratio of the first weight average molecular weight to the second weight average molecular weight (Mw1/Mw2).

Various types of polymer composition can be described as below:

Point at X=0/Y=0: An ideal case of absolutely narrow MWD and absolutely narrow SCBD. Practically impossible for X=0 due to the forced division along temperature axis into two halves, as shown in FIG. 1 and FIG. 2.

Line of X=0: An ideal case of broadening MWD while keeping SCBD absolutely narrow. At X=0, no difference in the direction of moving Y values up or down; i.e., broadening MWD while keeping SCBD at absolute narrow.

Line of Y=0: A case of broadening SCBD while keeping MWD unchanged and narrow.

Corner with X<0/Y<1: Products where polymer composition characterized by the combination of Low Mwi/Low Ti (high SCB) molecules with High Mwi/High Ti (low SCB) molecules; exemplified by conventional LLDPE with ZN-catalyst.

Corner with X<0/Y>1: Products where polymer composition characterized by the combination of Low Mwi/High Ti (low SCB) molecules with High Mwi/Low Ti (high SCB) molecules; exemplified by the so-called BOCD (Broad Orthogonal Composition Distribution) or Reversed Composition Distribution products.

Additional test methods include the following.

TABLE 1 Test Name Method Melt Index (MI) ASTM D-1238 2.16 kg (190° C.) (I₂) or (I_(2.16)) High Load Melt Index (HLMI) ASTM D-1238 21.6 kg (190° C.) (I₂₁) or (I_(21.6)) Melt Index Ratio (MIR) I₂₁/I₂ Density ASTM D1505, column density. Samples were molded under ASTM D4703-10a, Procedure C, then conditioned under ASTM D618-08 (23° ± 2° C. and 50 ± 10% Relative Humidity) for 40 Hours before testing 1% Secant Modulus Modified ASTM D-882, sample conditioning* Yield Strength Modified ASTM D-882, sample conditioning*, 4″ sample length Tensile Strength Modified ASTM D-882, sample conditioning*, 4″ sample length Elongation at Break Modified ASTM D-882, sample conditioning*, 4″ sample length Elongation at Yield Modified ASTM D-882, sample conditioning*, 4″ sample length Dart Drop Modified ASTM D-1709, Phenolic, Method A. Sample conditioning in the lab, calculation uses last 10 passes and 10 fails Haze ASTM D-1003 Gloss, 45° ASTM D-2457 Elmendorf Tear ASTM D1922 with ASTM Conditioning for 40 Hours at 23° ± 2° C. and 50 ± 10% Relative Humidity Puncture Modified ASTM D5748. ASTM probe was used with two 0.25 mil HDPE slip sheets. Machine Model: United SFM-1. Testing speed: 10 in/min. ¹NMR Unsaturations in a polymer and specifically percent internal unsaturation are determined by ¹H NMR with reference to 38 MACROMOLECULES 6988 (2005), and 47 MACROMOLECULES 3782 (2014). (see ¹HNMR section) Heat Seal 1 inch film strip of 1 mil gauge, sealed at various temperatures under 73 psi (0.5 N/mm²) for 1 second. Following ASTM Conditioning for 40 Hours at 23° ± 2° C. and 50 ± 10% Relative Humidity, the sealed specimen were tested in T-joint peel mode at 20 inch/min pulling speed. Hot tack 1 inch film strip of 1 mil gauge, sealed at various temperatures under 73 psi (0.5 N/mm²) for 0.5 second. After a 0.4 second delay, the sealed specimen were pulled at 200 mm/speed in T-joint peel mode. *the samples are cut from the rolls, placed between sheets of paper, and then placed on the counter before testing

EXAMPLES

It is to be understood that while the invention has been described in conjunction with the specific embodiments thereof, the foregoing description is intended to illustrate and not limit the scope of the invention. Other aspects, advantages and modifications will be apparent to those skilled in the art to which the invention pertains.

Therefore, the following examples are put forth so as to provide those skilled in the art with a complete disclosure and description and are not intended to limit the scope of that which the inventors regard as their invention.

All manipulations were performed in an inert N₂ purged glove box unless otherwise stated. All anhydrous solvents were purchased from Fisher Chemical and were degassed and dried over molecular sieves prior to use. Deuterated solvents were purchased from Cambridge Isotope Laboratories and dried over molecular sieves prior to use. n-Butyl lithium (2.5 M solution in hexane), diphenylsilyl dichloride (Ph₂SiCl₂), methylmagnesium bromide (3.0 M solution in diethyl ether) and trifluoromethanesulfonate (AgOTf) were purchased from Sigma-Aldrich. Hafnium tetrachloride (HfCl₄) 99+%, zirconium tetrachloride (ZrCl₄) 99+% were purchased from Strem Chemicals and TCI America, respectively, and used as received. Lithium-n-propylcyclopentadienide was purchased from Boulder Scientific. Potassium cyclopentadienide (KCp) was prepared in accordance with the description in Amsharov, K.; Abdurakhmanova, N.; Stepanow, S.; Rauschenbach, S.; Jansen, M.; Kern, K. Angew. Chem. Int. Ed. 2010, 49, 9392-9396. All other chemicals and materials were used as purchased unless otherwise stated.

Catalyst systems (i.e., mixed or dual catalyst systems) were prepared by the product of the combination of the following two catalysts (labeled as OMC2530 and AN) with the following methods and materials.

Synthesis of Diphenylsilyl-bis(trifluoromethanesulfonate), Ph₂Si(OTf)₂

Solid Ph₂SiCl₂ (20.0 g, 79.0 mmol) was dissolved in 250 mL of DCM and cooled to −25° C., and then was added to a solid silver trifluoromethanesulfonate (40.59 g, 158 mmol) over a period of 5-10 minutes. The resulting mixture was covered with aluminum foil and stirred overnight at about 23° C. Insoluble AgCl (byproduct) was filtered out and volatiles from the filtrate were removed in vacuo to yield a colorless crystalline solid of Ph₂Si(OTf)₂ in 36.66 g (94.6%) yield. ¹H NMR (400 MHz, CD₂Cl₂): δ 7.50-7.55 (4H, m, Ar—CH), 7.65-7.70 (2H, m, Ar—CH), 7.73-7.75 (4H, m, Ar—CH) ppm.

Synthesis of Diphenylsilyl-bis(n-propylcyclopentadiene), Ph₂Si(nPrCpH)₂

Solid Ph₂Si(OTf)₂ (36.7 g, 75.0 mmol) was slurried in 350 mL of diethyl ether and cooled to −25° C., and then was added to a solid lithium-n-propylcyclopentadienide (17.1 g, 150.0 mmol) over a period of 10-15 minutes. The resulting yellowish mixture was stirred overnight at about 23° C. to ensure completion of the reaction. All volatiles from the reaction mixture were removed in vacuo. The crude materials were extracted with hexane (60 mL×5) and followed by solvent removal to yield a pale yellow oil of Ph₂Si(nPrCpH)₂ in 30.2 g (98.6%) yield. ¹H NMR (400 MHz, C₆D₆): δ 0.84-0.99 (6H, m, nPr-CH₃), 1.45-1.60 (4H, m, nPr-CH₂), 2.29-2.35 (4H, m, nPr-CH₂), 3.89 (1H, s, Cp-CH), 4.06 (1H, s, Cp-CH), 6.26-6.80 (4H, m, Cp-CH), 7.00-7.07 (1H, m, Cp-CH), 7.18-7.30 (6H, m, Ar—CH), 7.53 (1H, d, J_(HH)=6.72 Hz, Cp-CH), 7.68-7.81 (4H, m, Ar—CH) ppm.

Synthesis of Lithium diphenylsilyl-bis(n-propylcyclopentadienide), Ph₂Si(nPrCp)₂Li₂

Solid Ph₂Si(^(n)Pr-CpH)₂ (35.42 g, 140 mmol) was dissolved in 350 mL of THF and cooled to −25° C., and then was added to a hexane solution of n-butyl lithium (70.1 mL, 175.2 mmol, 2.02 equivalents) over a period of 45-60 minutes. The resulting mixture was gradually warmed to at about 23° C. and continuously stirred overnight. All volatiles from the reaction mixture were removed in vacuo, and triturated with hexane to evaporate traces of THF. The materials were thoroughly washed with hexane to remove any soluble impurities and dried under vacuum to give an off-white solid of Ph₂Si(nPrCp)₂Li₂ in 30.7 g (87%) yield. ¹H NMR (400 MHz, THF-d₈): δ 0.90 (6H, t, J_(HH)=7.36 Hz, nPr-CH₃), 1.54 (4H, qt, J_(HH)=7.44 Hz, nPr-CH₂), 2.46 (4H, t, J_(HH)=7.48 Hz, nPr-CH₂), 5.74 (2H, t, J_(HH)=2.2 Hz, Cp-CH), 5.89 (2H, t, J_(HH)=2.1 Hz, Cp-CH), 5.95 (2H, t, J_(HH)=2.2 Hz, Cp-CH), 7.07-7.09 (6H, m, Ar—CH), 7.58-7.60 (4H, m, Ar—CH) ppm.

Synthesis of Diphenylsilyl-bis(n-propylcyclopentadienyl)hafnium dichloride, Ph₂Si(nPr-Cp)₂HfCl₂ (Catalyst 1 (AN))

Solid HfCl₄ (24.04 g, 75.2 mmol) was slurried in 400 mL of diethyl ether and cooled to −25° C., and this was added to a solid Ph₂Si(nPrCp)₂Li₂ (30.7 g, 75.2 mmol) over a period of 15-20 minutes. The resulting mixture was stirred overnight at about 23° C. Insoluble materials were removed by filtration and subsequently volatiles from the filtrate were removed in vacuo. The crude materials were first washed with cold hexane and then extracted with diethyl ether, followed by solvent removal to yield a pale yellow semi-solid of Ph₂Si(nPrCp)₂HfCl₂ in 16.54 g (34.2%) yield. ¹H NMR (400 MHz, CD₂Cl₂): δ 0.95 (6H, t, J_(HH)=7.4 Hz, nPr-CH₃), 1.54-1.64 (4H, m, nPr-CH₂), 2.57-2.76 (4H, m, nPr-CH₂), 5.52 (1H, t, J_(HH)=2.4 Hz, Cp-CH), 5.62 (1H, t, J_(HH)=2.4 Hz, Cp-CH), 5.84 (1H, t, J_(HH)=2.8 Hz, Cp-CH), 5.97 (1H, t, J_(HH)=2.8 Hz, Cp-CH), 6.53 (1H, t, J_(HH)=2.2 Hz, Cp-CH), 6.62 (1H, t, J_(HH)=2.2 Hz, Cp-CH), 7.47-7.55 (6H, m, Ar—CH), 7.89-7.96 (4H, m, Ar—CH) ppm.

Synthesis of Rac-meso-diphenylsilyl-bis(n-propylcyclopentadienyl)hafnium dimethyl, Ph₂Si(nPrCp)₂HfMe₂

Solid Ph₂Si(nPrCp)₂HfCl₂ (16.54 g, 25.7 mmol) was dissolved in 250 mL of diethyl ether and cooled to −25° C., and then was added to an ethereal solution of MeMgBr (17.3 mL, 51.9 mmol) over a period of 45-60 minutes. The resulting mixture was gradually warmed to about 23° C. and continuously stirred overnight. Insoluble materials were removed by filtration through a pad of celite. Volatiles from the filtrate were removed under reduced pressure, and then extracted with hexane (50 mL×4). Solvent removal in vacuo yielded a pale yellow oil of rac,meso-Ph₂Si(nPrCp)₂HfMe₂ in 12.2 g (78.7%) yield. The ¹H NMR spectrum of the final material integrated a ˜1:1 ratio of rac/meso isomers. ¹H NMR (400 MHz, CD₂Cl₂): δ −0.46 (3H, s, Hf—CH₃, meso), δ −0.41 (6H, s, Hf—CH₃, rac), δ −0.33 (3H, s, Hf—CH₃, meso), 0.93-0.97 (12H, m, nPr-CH₃), 1.60 (8H, qt, J_(HH)-=7.4 Hz, nPr-CH₂), 2.45-2.64 (8H, m, nPr-CH₂), 5.41-5.44 (4H, m, Cp-CH), 5.56 (2H, t, J_(HH)=2.8 Hz, Cp-CH), 5.60 (2H, t, J_(HH)=2.7 Hz, Cp-CH), 6.40 (2H, t, J_(HH)=2.4 Hz, Cp-CH), 6.43 (2H, t, J_(HH)=2.6 Hz, Cp-CH), 7.17-7.20 (12H, m, Ar—CH), 7.82-7.86 (8H, m, Ar—CH) ppm.

Supported Catalyst Syntheses: Rac,Meso-pH₂Si(nPrCp)₂HfMe₂ (OMC2530): Meso-O(Me2SiInd)₂ZrCl₂ (AN), 75:25 Mole Ratio

To a stirred vessel 1400 g of toluene was added along with 925 g of methylaluminoxane (30 wt % in toluene). To this solution 734 g of ES70—875° C. calcined silica was added. The mixture was then stirred for three hours at 100° C. after which the temperature was reduced and the reaction was allowed to cool to about 23° C. Diphenylsilylbis(n-propylcyclopentadienide) hafnium (IV) dimethyl (18.1 g, 30.0 mmol) (OMC2530) and meso-O(Me2SiInd)₂ZrCl₂ (5.22 g, 10.0 mmol) (AN) were then dissolved in toluene (250 g) and added to the vessel, which was stirred for two more hours. meso-O(Me2SiInd)₂ZrCl₂ was prepared as described in Example 1A of U.S. Pat. No. 7,060,765. The mixing speed was then reduced and stirred slowly while drying under vacuum for 60 hours, after which 998 g of light yellow silica material was obtained to yield a dual supported catalyst.

Polymerization Process

Polymerization processes were performed using the catalyst system prepared above in an 18.5 foot tall gas-phase fluidized bed reactor with a 10 foot body and an 8.5 foot expanded section. Cycle and feed gases were fed into the reactor body through a perforated distributor plate, and the reactor was controlled at 300 psi and 70 mol % ethylene. The reactor temperature was maintained at 185° F. throughout the polymerization by controlling the temperature of the cycle gas loop. The catalyst system as described above was delivered in a mineral oil slurry containing 20 wt % supported catalyst. Hydrogen was lowered and hexene was increased relative to standard (nPr)HfMe2 catalyst. Overall, the OMC2530:AN pair at an 75:25 ratio showed a lower composite molecular weight capability and poorer composite incorporation than the standard catalyst. However, at these temperatures and conditions the overall composition and molecular weight distribution resulted in a higher MIR. The relative MW capability and comonomer incorporation of these two catalysts create a desirable product after polymerization that can be tuned by adjusting catalyst ratio and reactor conditions. Details regarding the process and product may be found in Table 2, Table 3, Table 4, and Table 5. The process conditions were varied to obtain and demonstrate a balance of properties, for example, high stiffness and toughness, good sealing performance, and good optical properties such as haze and gloss. (nPr)HfMe2 catalyst (References/Comp.) is capable of producing a BOCD polymer product but lacks improvements in certain properties such as stiffness.

TABLE 2 Inventive Inventive Reference Exp. A Exp. B Comp. Process Data Catalyst # OMC2530:AN OMC2530:AN (nPr)HfMe2, 2 (75:25), 1 (75:25), 1 Trim — — — H2 conc. (molppm) 238 199 348 C6/C2 Ratio (mol %/mol %) 0.018 0.019 0.013 Comonomer conc. (mol %) 1.24 1.36 0.90 C2 conc. (mol %) 69.9 70.2 69.9 Comonomer/C2 Flow Ratio 0.092 0.097 0.079 H2/C2 Ratio (ppm/mol %) 3.4 2.8 5.0 Rx. Pressure SP (psig) 300 300 300 Reactor Temp SP (F.) 185 185 185 Avg. Bedweight (lb) 316 318 322 Production (lb/hr) 56 61 70 Residence Time (hr) 5.7 5.2 4.6 Avg Velocity (ft/s) 2.25 2.25 2.25 Catalyst Slurry Feed (cc/hr) or Secs/Shot 40.0 40.0 40.0 Catalyst Slurry Conc. (wt frac.) 0.2 0.2 0.2 Catalyst Slurry Density (g/ml) 0.94 0.94 0.94 Trim Feed (ml/hr) 0.00 0.00 0.00 Catalyst Feed (g/hr) 7.548 7.559 7.548 Cat Activity (g poly/g cat) 3342 3674 3342 Product Data Melt Index (MI) (g/10 min) 1.12 0.86 1.04 HLMI (g/10 min) 32.09 24.78 23.32 HLMI/MI Ratio 28.59 28.71 22.43 Gradient Density (g/cc) 0.9205 0.9195 0.9180 Bulk Density (g/cc) 0.4258 0.4229 0.4487

TABLE 3 Gas Phase Polymerization of Ethylene and 1-Hexene Mixed MI Mw Mn Hexene Catalysts dg/min MIR g/mol g/mol Mz g/mol Mz/Mn Mw/Mn Mz/Mw wt % g′(vis) 1 exp A 1.12 29 117964 13036 284666 21.8 9.0 2.4 8.96 0.957 1 exp B 0.86 29 130155 17982 313031 17.4 7.2 2.4 10.16 0.988 2 Comp. 1.04 22 119537 23477 240418 10.2 5.1 2.0 7.88 1.012

TABLE 4 Gas Phase Polymerization of Ethylene and 1-Hexene Mixed MI RCI, m Catalysts dg/min MIR (kg/mol) CDR2, m T₇₅-T₂₅(° C.) 1 exp A 1.12 29 149.8 1.85 46.1 1 exp B 0.86 29 155.1 1.78 44.1 2 Comp. 1.04 22 75.0 1.53 34.7

TABLE 5 Level of unsaturation (internal (I) and terminal (T)) for inventive polyethylenes from mixed cat. system 1 exp. A Vy1 and Vy2 (I) 0.02 Vy5 (T) 0.01 Tri-substituted olefins (I) 0.01 Vinyls (T) 0.02 Vinylidenes (T) 0.01 total internal unsaturations 0.03 Total unsaturation per 1000 carbons 0.07

Table 6 further shows a comparison between inventive PE compositions and commercially available resins.

TABLE 6 Mw1/ Tw1 − Description Mw1 Mw2 Tw1 Tw2 Mw2 Tw2 (log(Mw1/Mw2))/(Tw1 − Tw2) 1 exp A 190,937 115,590 59.3 90.4 1.65 −31.1 −0.0070 Exceed 1018 163,239 156,716 72.4 86.9 1.04 −14.5 −0.0012 (919/1.0/16) Enable 2010 103,550 136,434 75.9 82.5 0.76 −6.7 0.0179 (920/1.1/34) Evolue 3010 148,115 166,038 60.3 88.4 0.89 −28.1 0.0018 (926/0.8/n.a.) Elite 5400 174,160 109,611 62.0 85.8 1.59 −23.8 −0.0085 (918/1.1/32) Dowlex 2045 117,305 238,061 66.4 88.0 0.49 −21.6 0.0142 (920/1.0/29) Borstar FB 2230 268,435 371,505 53.5 91.4 0.72 −37.9 0.0037 (923/0.2/110) Dowlex ™ 2045 polyethylene, Borstar ™ FB2230 polyethylene, Evolue ™ 3010 polyethylene, Elite ™ 5400 polyethylene, and Exceed ™ 1018 and Enable ™ 2010 polyethylenes are all commercially available and may be obtained from The Dow Chemical Company, the Borealis Group, Prime Polymer Co., Ltd., The Dow Chemical Company, and ExxonMobil Chemical Company, respectively. Film Production

Blown film evaluations of the inventive polymers as prepared and described above were carried out on a Gloucester line at 60 mil die gap and 2.5 BUR. Film properties at 1.0 mil gauge are summarized below in Table 7.

TDA is the total defect area. It is a measure of defects in a film specimen, and reported as the accumulated area of defects in square millimeters (mm²) normalized by the area of film in square meters (m²) examined, thus having a unit of (mm²/m²) or “ppm”. In Table 7, only defects with a dimension above 200 microns are reported.

TDA is obtained by an Optical Control System (OCS). This system consists of a small extruder (ME20 2800), cast film die, chill roll unit (Model CR-9), a winding system with good film tension control, and an on-line camera system (Model FSA-100) to examine the cast film generated for optical defects. The typical testing condition for the cast film generation is given below:

-   -   Extruder temperature setting (° C.): Feed throat/Zone 1/Zone         2/Zone 3/Zone 4/Die: 70/190/200/210/215/215     -   Extruder speed: 50 rpm     -   Chill roll temperature: 30° C.     -   Chill roll speed: 3.5 m/min

The system generates a cast film of about 4.9 inch in width and a nominal gauge of 2 mil. Melt temperature varies with materials, and is typically around 215° C.

ESO is the Energy specific output, is the extrusion output (lb/hr) in film extrusion normalized by the extruder power (hp) consumption and is a measure of a material's processability.

TABLE 7 Exceed XP Exceed XP Exceed XP OMC2530:AN OMC2530:AN Exceed R-123 dry R123 slurry Exceed XP R123 slurry (75:25) (75:25) 1018HA 175F 175F R-123 185F 185F 1 Exp. A 1 Exp. B I2 (g/10 min) — 0.99 0.95 0.75 1.01 1.13 0.85 I21 (g/10 min) — 27.52 28.24 16.59 23.31 33.85 24.99 MIR — 27.8 29.7 22.1 23.1 30.0 29.4 density — 0.9207 0.9192 — 0.9188 0.9217 0.9209 (g/cm3) Melt (° F.) 409 — — 408 401 395 401 Motor load, % 64.8 58.3 — 63.4 59.5 54.7 59.3 ESO 8.96 — — 8.95 9.68 10.84 9.86 (lb/HP/hr) Film gauge 0.96 1.00 0.98 0.97 0.98 1.01 0.97 (mils) 1% Secant (psi) MD 26,101 31,608 30,388 31,137 26083 37275 35436 TD 29,745 39,374 39,761 39,163 31354 51542 47833 AVG 27,923 35,491 35,075 35,150 28,719 44,408 41,635 Puncture Peak 11.5 10.4 10.0 11.8 10.5 9.7 9.9 Force (lbs/mil) Puncture 35.5 30.7 29.0 34.0 32.2 27.3 26.8 Break Energy (in-lbs/mil) Dart Drop, 643 782 908 430 602 277 422 g/mil Elmendorf Tear, g/mil MD 235 264 223 375 272 175 323 TD 440 459 455 537 482 718 712 Haze, % >30 >30 28.0 13.0 19.0 11.4 9.3 Gloss, % MD 31.0 29.0 29.0 45.5 37.0 45.6 53.0 TD 32.0 32.0 31.0 48.1 34.0 45.4 55.8 Seal Initiation 98.7 — — — — 92.6 90.0 Temperature at 1N force (° C.) Seal 102.8 — — — — 99.7 97.0 Temperature at 5N force (° C.) Maximum Seal 10.0 — — — — 12.5 12.4 force (N) Hot Tack 98.8 — — — — 94.5 90.5 Initiation Temperature at 1N force (° C.) Hot Tack 102.8 — — — — 97.7 97.2 Temperature at 5N force (° C.) Maximum Hot 11.5 — — — — 8.6 13.4 Tack force (N) Film gauge — 3.11 2.83 — 3.07 2.99 2.98 (mils) 1% Secant (psi) MD — 32,807 31,219 — 29514 35215 34282 TD — 37,946 36,959 — 32,543 54653 54134 AVG — 35,377 34,089 — 31,029 44,934 44,208 Dart Drop, — 411.6 444 — 336 206 244.3 g/mil (stainless steel dart) Elmendorf Tear, g/mil MD — 328 305 — 325.2 300 308.7 TD — 409 408 — 378.5 511.1 512.9 Puncture Peak — 6.6 7.0 — — 7.0 6.9 Force (lbs/mil) Puncture — 15.8 16.9 — — 18.3 18.0 Break Energy (in-lbs/mil)

FIG. 4 shows the average MD/TD film modulus as a function of resin density for both comparative examples as well as the inventive examples. The equation (Eq-3) below shows the film modulus dependence of comparative examples on its resin density. All the inventive examples exhibited a substantial advantage in film stiffness at a given resin density. Average Modulus=Constant 1(C1)*Density−Constant 2(C2)  (Eq-3)

In a class of embodiments, the film exhibits a relationship between average MD/TD modulus and density satisfying the following equation: Avg. Modulus≥1.2*(C1*Density−C2);

-   -   and, in particular as an example,         Average Modulus≥1.2*(2,065,292*Density−1,872,345).

A good balance of various performance attributes has been an important goal in the development of new polyethylene compositions. For LLDPE film applications and products, key performance attributes include one or more of stiffness, toughness, optical properties, and processability. For some very important LLDPE film applications, sealing performance is also important. Sealing performance is affected mainly by density. Sealing performance generally improves as density gets lower but density typically has the opposite effect on stiffness. Therefore, to achieve a balanced performance, there is usually a trade-off between stiffness and sealing performance.

In particular, for polyethylene compositions, the molecular weight and distribution and comonomer distribution interdependence (e.g., MWD×CD), has a strong effect on sealing performance, with narrow CD resin made from metallocene catalysts outperforming broad CD resin by conventional catalysts. To improve sealing performance while maintaining good stiffness is difficult. As demonstrated above, the dual or mixed catalyst system providing BCD and BOCD benefits yield PE LLDPE films with the ideal combination of high stiffness and good sealing performance, as well as good optical properties.

The phrases, unless otherwise specified, “consists essentially of” and “consisting essentially of” do not exclude the presence of other steps, elements, or materials, whether or not, specifically mentioned in this specification, so long as such steps, elements, or materials, do not affect the basic and novel characteristics of the invention, additionally, they do not exclude impurities and variances normally associated with the elements and materials used.

For the sake of brevity, only certain ranges are explicitly disclosed herein. However, ranges from any lower limit may be combined with any upper limit to recite a range not explicitly recited, as well as, ranges from any lower limit may be combined with any other lower limit to recite a range not explicitly recited, in the same way, ranges from any upper limit may be combined with any other upper limit to recite a range not explicitly recited. Additionally, within a range includes every point or individual value between its end points even though not explicitly recited. Thus, every point or individual value may serve as its own lower or upper limit combined with any other point or individual value or any other lower or upper limit, to recite a range not explicitly recited.

All priority documents are herein fully incorporated by reference for all jurisdictions in which such incorporation is permitted and to the extent such disclosure is consistent with the description of the present invention. Further, all documents and references cited herein, including testing procedures, publications, patents, journal articles, etc. are herein fully incorporated by reference for all jurisdictions in which such incorporation is permitted and to the extent such disclosure is consistent with the description of the present invention.

While the invention has been described with respect to a number of embodiments and examples, those skilled in the art, having benefit of this disclosure, will appreciate that other embodiments can be devised which do not depart from the scope and spirit of the invention as disclosed herein. 

What is claimed is:
 1. A polyethylene composition comprising at least 65 wt % ethylene derived units and from 0 to 35 wt % of C₃-C₁₂ olefin comonomer derived units, based upon the total weight of the polyethylene composition, wherein the polyethylene composition has: a) an RCI,m of 125 kg/mol or greater; b) an internal unsaturation as measured by 1H NMR less than 0.30 total internal unsaturations per thousand carbon atoms; c) a Tw₁-Tw₂ value of from −16 to −38° C.; d) an Mw₁/Mw₂ value within the range from 0.9 to 4; and one or more of the following: e) a density of from 0.890 g/cm3 to 0.940 g/cm³; f) a melt index (MI) of from 0.1 g/10 min to 30 g/10 min; g) a melt index ratio (I₂₁/I₂) of from 10 to 90; h) an M_(w)/M_(n) of from 2 to 12; i) an M_(z)/M_(w) of from 2.2 to 5.0; j) an M_(z)/M_(n) of from 10 to 40; and k) a g′ (vis) of 0.990 or less.
 2. The polyethylene composition of claim 1, wherein the polyethylene composition comprises from 0.5 to 20 wt % of the C₃-C₁₂ olefin comonomer derived units, based upon the total weight of the polyethylene composition.
 3. The polyethylene composition of claim 1, wherein the polyethylene composition has a Tw₁-Tw₂ value of from −23 to −36° C.
 4. The polyethylene composition of claim 1, wherein the polyethylene composition has a Tw₁-Tw₂ value of from −23 to −33° C.
 5. The polyethylene composition of claim 1, wherein the polyethylene composition has an Mw₁/Mw₂ value of from 1.25 to
 4. 6. The polyethylene composition of claim 1, wherein the polyethylene composition has a melt index (MI) of from 0.1 g/10 min to 6 g/10 min.
 7. The polyethylene composition of claim 1, wherein the polyethylene composition has a melt index ratio (I₂₁/I₂) of from 20 to
 45. 8. The polyethylene composition of claim 1, wherein the polyethylene composition has an M_(w)/M_(n) of from 5 to
 10. 9. The polyethylene composition of claim 1, wherein the polyethylene composition has a g′(vis) of 0.989 or less.
 10. The polyethylene composition of claim 1, wherein the polyethylene composition has a density of from 0.912 g/cm3 to 0.922 g/cm3.
 11. The polyethylene composition of claim 1, wherein the internal unsaturation of the polyethylene composition as measured by ¹H NMR is less than 0.20 total internal unsaturations per thousand carbon atoms.
 12. The polyethylene composition of claim 1, wherein the internal unsaturation of the polyethylene composition as measured by ¹H NMR is less than 0.10 total internal unsaturations per thousand carbon atoms.
 13. A film made from the polyethylene composition of claim 1, wherein the film has: i) a relationship between MD/TD modulus and density that satisfies the following equation: Avg. Modulus≥1.2*(2,065,292*Density−1,872,345); and ii) a seal initiation temperature at 1 N of ≤98.0° C.
 14. The film of claim 13, wherein the film is a blown film or cast film.
 15. The film of claim 13, wherein the seal initiation temperature at 1 N is ≤97.0° C.
 16. The film of claim 13, wherein the seal initiation temperature at 1 N is ≤95.0° C.
 17. The film of claim 13, wherein the seal initiation temperature at 5 N is ≤102.0° C.
 18. The film of claim 13, wherein the seal initiation temperature at 5 N is ≤100.0° C.
 19. The film of claim 13, wherein the seal initiation temperature at 5 N is ≤99.0° C.
 20. The film of claim 13, wherein the film exhibits an average 1% secant MD/TD modulus of 35,000 psi or greater.
 21. The film of claim 13, wherein the film exhibits an average 1% secant MD/TD modulus of 40,000 psi or greater.
 22. The film of claim 13, wherein the film has a dart drop impact resistance of 200 g/mil or greater. 